Polyester compositions containing cyclobutanediol having a certain combination of inherent viscosity and moderate glass transition temperature and articles made therefrom

ABSTRACT

Described are polyesters comprising (a) a dicarboxylic acid component comprising terephthalic acid residues; optionally, aromatic dicarboxylic acid residues or aliphatic dicarboxylic acid residues; 2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and 1,4-cyclohexanedimethanol residues. The polyesters may be manufactured into articles such as fibers, films, bottles or sheets.

CROSS-REFERENCES TO RELATED APPLICATIONS

This application claims priority under 35 U.S.C. §119(e) to U.S.Provisional Application Ser. No. 60/691,567 filed on Jun. 17, 2005, U.S.Provisional Application Ser. No. 60/731,454 filed on Oct. 28, 2005, U.S.Provisional Application Ser. No. 60/731,389, filed on Oct. 28, 2005,U.S. Provisional Application Ser. No. 60/739,058, filed on Nov. 22,2005, and U.S. Provisional Application Ser. No. 60/738,869, filed onNov. 22, 2005, U.S. Provisional Application Ser. No. 60/750,692 filed onDec. 15, 2005, U.S. Provisional Application Ser. No. 60/750,693, filedon Dec. 15, 2005, U.S. Provisional Application Ser. No. 60/750,682,filed on Dec. 15, 2005, and U.S. Provisional Application Ser. No.60/750,547, filed on Dec. 15, 2005, all of which are hereby incorporatedby this reference in their entireties.

FIELD OF THE INVENTION

The present invention generally relates to polyester compositions madefrom terephthalic acid or an ester thereof or mixtures thereof;2,2,4,4-tetramethyl-1,3-cyclobutanediol; and 1,4-cyclohexanedimethanolhaving a certain combination of inherent viscosity and glass transitiontemperature (Tg). These compositions have a unique combination of atleast two of high impact strengths, moderate glass transitiontemperature (T_(g)), toughness, certain inherent viscosities, lowductile-to-brittle transition temperatures, good color and clarity, lowdensities, chemical resistance, and long crystallization half-times,which allow them to be easily formed into articles.

BACKGROUND OF THE INVENTION

Poly(1,4-cyclohexylenedimethylene terephthalate) (PCT), a polyesterbased solely on terephthalic acid or an ester thereof and1,4-cyclohexanedimethanol, is known in the art and is commerciallyavailable. This polyester crystallizes rapidly upon cooling from themelt, making it very difficult to form amorphous articles by methodsknown in the art such as extrusion, injection molding, and the like. Inorder to slow down the crystallization rate of PCT, copolyesters can beprepared containing additional dicarboxylic acids or glycols such asisophthalic acid or ethylene glycol. These ethylene glycol- orisophthalic acid-modified PCTs are also known in the art and arecommercially available.

One common copolyester used to produce films, sheeting, and moldedarticles is made from terephthalic acid, 1,4-cyclohexanedimethanol, andethylene glycol. While these copolyesters are useful in many end-useapplications, they exhibit deficiencies in properties such as glasstransition temperature and impact strength when sufficient modifyingethylene glycol is included in the formulation to provide for longcrystallization half-times. For example, copolyesters made fromterephthalic acid, 1,4-cyclohexanedimethanol, and ethylene glycol withsufficiently long crystallization half-times can provide amorphousproducts that exhibit what is believed to be undesirably higherductile-to-brittle transition temperatures and lower glass transitiontemperatures than the compositions revealed herein.

The polycarbonate of 4,4′-isopropylidenediphenol (bisphenol Apolycarbonate) has been used as an alternative for polyesters known inthe art and is a well known engineering molding plastic. Bisphenol Apolycarbonate is a clear, high-performance plastic having good physicalproperties such as dimensional stability, high heat resistance, and goodimpact strength. Although bisphenol-A polycarbonate has many goodphysical properties, its relatively high melt viscosity leads to poormelt processability and the polycarbonate exhibits poor chemicalresistance. It is also difficult to thermoform.

Polymers containing 2,2,4,4-tetramethyl-1,3-cyclobutanediol have alsobeen generally described in the art. Generally, however, these polymersexhibit high inherent viscosities, high melt viscosities, and high glasstransition temperatures such that the equipment used in industry can beinsufficient to manufacture or post polymerization process thesematerials.

Thus, there is a need in the art for a polymer having a combination oftwo or more properties, chosen from at least one of the following:toughness, moderate glass transition temperatures, good impact strength,hydrolytic stability, chemical resistance, long crystallizationhalf-times, low ductile to brittle transition temperatures, good colorand clarity, lower density and/or thermoformability of polyesters whileretaining processability on the standard equipment used in the industry.

SUMMARY OF THE INVENTION

It is believed that certain compositions made from terephthalic acid, anester thereof, or mixtures thereof; 1,4-cyclohexanedimethanol; and2,2,4,4-tetramethyl-1,3-cyclobutanediol with a certain combination ofinherent viscosities and/or glass transition temperatures are superiorto polyesters known in the art and to polycarbonate with respect to atleast one of the following: of high impact strengths, hydrolyticstability, toughness, chemical resistance, good color and clarity, longcrystallization half-times, low ductile to brittle transitiontemperatures, lower specific gravity and thermoformability. Thesecompositions are believed to be similar to polycarbonate in heatresistance and are still processable on the standard industry equipment.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 1 to 99 mole % of 2,2,4,4-tetramethyl-1,3-cyclobutanediol            residues; and        -   ii) 1 to 99 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity is 0.10 to less than 1.0 dL/g            as determined in 60/40 (wt/wt) phenol/tetrachloroethane at a            concentration of 0.5 g/100 ml at 25° C.; and            wherein the polyester has a Tg of 85 to 120° C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 1 to 99 mole % of 2,2,4,4-tetramethyl-1,3-cyclobutanediol            residues; and        -   ii) 1 to 99 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity is 0.35 to less than 1.0 dL/g            as determined in 60/40 (wt/wt) phenol/tetrachloroethane at a            concentration of 0.5 g/100 ml at 25° C.; and            wherein the polyester has a Tg of 85 to 120° C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 5 to less than 50 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) greater than 50 to 95 mole % of            1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to 1.2 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and            wherein the polyester has a Tg of 85 to 120° C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 10 to 30 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 70 to 90 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to 1.2 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and            wherein the polyester has a Tg of 85 to 120° C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 15 to 25 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 75 to 85 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity is from 0.50 to 1.2 dL/g as            determined in 60/40 (wt/wt) phenol/tetrachloroethane at a            concentration of 0.5 g/100 ml at 25° C.; and            wherein the polyester has a Tg of 85 to 120° C.

In one aspect, this invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 5 to less than 50 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) greater than 50 to 95 mole % of            1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to 1.2 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 95 to 115°            C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 10 to 30 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 70 to 90 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to 1.2 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 95 to 115°            C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 15 to 25 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 75 to 85 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to 1.2 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 95 to 115°            C.

In one aspect, this invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 5 to less than 50 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) greater than 50 to 95 mole % of            1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to less than 0.75 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 85 to 120°            C.

In one aspect, this invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 10 to 30 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 70 to 90 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to less than 0.75 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 85 to 120°            C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 15 to 25 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 75 to 85 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to less than 0.75 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 85 to 120°            C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 5 to less than 50 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) greater than 50 to 95 mole % of            1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to less than 0.75 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 95 to 115°            C.

In one aspect, this invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 10 to 30 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 70 to 90 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to less than 0.75 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 95 to 115°            C.

In one aspect, this invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 15 to 25 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 75 to 85 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.50            to less than 0.75 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 95 to 115°            C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 15 to 25 mole % of            2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and        -   ii) 75 to 85 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity of the polyester is from 0.60            to 0.72 dL/g as determined in 60/40 (wt/wt)            phenol/tetrachloroethane at a concentration of 0.5 g/100 ml            at 25° C.; and wherein the polyester has a Tg of 95 to 115°            C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 1 to 99 mole % of 2,2,4,4-tetramethyl-1,3-cyclobutanediol            residues; and        -   ii) 1 to 98.99 mole % of 1,4-cyclohexanedimethanol residues,        -   iii) 0.01 to less than 15 mole % ethylene glycol;            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity is 0.35 to 1.2 dL/g as            determined in 60/40 (wt/wt) phenol/tetrachloroethane at a            concentration of 0.5 g/100 ml at 25° C.; and            wherein the polyester has a Tg of 85 to 120° C.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms; and    -   (b) a glycol component comprising:        -   i) 1 to 99 mole % of 2,2,4,4-tetramethyl-1,3-cyclobutanediol            residues; and        -   ii) 1 to 99 mole % of 1,4-cyclohexanedimethanol residues,            wherein the total mole % of the dicarboxylic acid component            is 100 mole %, and the total mole % of the glycol component            is 100 mole %; and            wherein the inherent viscosity is 0.35 to 1.2 dL/g as            determined in 60/40 (wt/wt) phenol/tetrachloroethane at a            concentration of 0.5 g/100 ml at 25° C.; and            wherein the polyester has a Tg of 85 to 120° C.; and            optionally, wherein one or more branching agents is added            prior to or during the polymerization of the polyester.

In one aspect, the invention relates to a polyester compositioncomprising at least one polyester which comprises:

-   -   (a) a dicarboxylic acid component comprising:        -   i) 70 to 100 mole % of terephthalic acid residues;        -   ii) 0 to 30 mole % of aromatic dicarboxylic acid residues            having up to 20 carbon atoms; and        -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid residues            having up to 16 carbon atoms;    -   (b) a glycol component comprising:        -   i) 1 to 99 mole % of 2,2,4,4-tetramethyl-1,3-cyclobutanediol            residues; and        -   ii) 1 to 99 mole % of 1,4-cyclohexanedimethanol residues;            and    -   (c) residues from at least one branching agent;        wherein the total mole % of the dicarboxylic acid component is        100 mole %, and the total mole % of the glycol component is 100        mole %; and        wherein the inherent viscosity is 0.35 to 1.2 dL/g as determined        in 60/40 (wt/wt) phenol/tetrachloroethane at a concentration of        0.5 g/100 ml at 25° C.; and        wherein the polyester has a Tg of 85 to 120° C.

In one aspect, this invention relates to a polyester compositioncomprising:

-   -   at least one polyester which comprises:        -   (a) a dicarboxylic acid component comprising:            -   i) 70 to 100 mole % of terephthalic acid residues;            -   ii) 0 to 30 mole % of aromatic dicarboxylic acid                residues having up to 20 carbon atoms; and            -   iii) 0 to 10 mole % of aliphatic dicarboxylic acid                residues having up to 16 carbon atoms; and        -   (b) a glycol component comprising:            -   i) 1 to 99 mole % of                2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and            -   ii) 1 to 99 mole % of 1,4-cyclohexanedimethanol                residues; and    -   at least one thermal stabilizer or reaction products thereof;        wherein the total mole % of the dicarboxylic acid component is        100 mole %, and the total mole % of the glycol component is 100        mole %; and        wherein the inherent viscosity of the polyester is 0.35 to 1.2        dL/g as determined in 60/40 (wt/wt) phenol/tetrachloroethane at        a concentration of 0.5 g/100 ml at 25° C.; and        wherein the polyester has a Tg of 85 to 120° C.

In one aspect, the polyester compositions useful in the inventioncontain at least one polycarbonate.

In one aspect, the polyester compositions useful in the inventioncontain no polycarbonate.

In one aspect, the polyesters useful in the invention contain less than15 mole % ethylene glycol residues, such as, for example, 0.01 to lessthan 15 mole % ethylene glycol residues

In one aspect, the polyesters useful in the invention contain noethylene glycol residues

In one aspect, the polyester compositions useful in the inventioncontain at least one thermal stabilizer and/or reaction productsthereof.

In one aspect, the polyesters useful in the invention contain nobranching agent or, alternatively, at least one branching agent is addedeither prior to or during polymerization of the polyester.

In one aspect, the polyesters useful in the invention contain at leastone branching agent without regard to the method or sequence in which itis added.

In one aspect, the polyesters useful in the invention are made from no1,3-propanediol, or 1,4-butanediol, either singly or in combination. Inother aspects, 1,3-propanediol or 1,4-butanediol, either singly or incombination, may be used in the making of the polyesters useful in thisinvention.

In one aspect of the invention, the mole % ofcis-2,2,4,4-tetramethyl-1,3-cyclobutanediol useful in certain polyestersuseful in the invention is greater than 50 mole % or greater than 55mole % of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol or greater than 70mole % of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol; wherein the totalmole percentage of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol andtrans-2,2,4,4-tetramethyl-1,3-cyclobutanediol is equal to a total of 100mole %.

In one aspect of the invention, the mole % of the isomers of2,2,4,4-tetramethyl-1,3-cyclobutanediol useful in certain polyestersuseful in the invention is from 30 to 70 mole % ofcis-2,2,4,4-tetramethyl-1,3-cyclobutanediol or from 30 to 70 mole % oftrans-2,2,4,4-tetramethyl-1,3-cyclobutanediol, or from 40 to 60 mole %of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol or from 40 to 60 mole %of trans-2,2,4,4-tetramethyl-1,3-cyclobutanediol, wherein the total molepercentage of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol andtrans-2,2,4,4-tetramethyl-1,3-cyclobutanediol is equal to a total of 100mole %.

In one aspect, the polyester compositions are useful in articles ofmanufacture including, but not limited to, extruded, calendered, and/ormolded articles including, but not limited to, injection moldedarticles, extrusion articles, cast extrusion articles, profile extrusionarticles, melt spun articles, thermoformed articles, extrusion moldedarticles, injection blow molded articles, injection stretch blow moldedarticles, extrusion blow molded articles and extrusion stretch blowmolded articles. These articles can include, but are not limited to,films, bottles, containers, sheet and/or fibers.

Also, in one aspect, use of these particular polyester compositionsminimizes and/or eliminates the drying step prior to melt processingand/or thermoforming.

In one aspect, the polyester compositions are useful in the inventionmay be used in various types of film and/or sheet, including but notlimited to extruded film(s) and/or sheet(s), calendered film(s) and/orsheet(s), compression molded film(s) and/or sheet(s), solution castedfilm(s) and/or sheet(s). Methods of making film and/or sheet include butare not limited to extrusion, calendering, compression molding, andsolution casting.

Also, in one aspect, use of these particular polyester compositionsminimizes or eliminates the drying step prior to melt processing and/orthermoforming.

In one aspect, the polyesters useful in the invention can be amorphousor semicrystalline. In one aspect, certain polyesters useful in theinvention can have a relatively low crystallinity. Certain polyestersuseful in the invention can thus have a substantially amorphousmorphology, meaning that the polyesters comprise substantially unorderedregions of polymer.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graph showing the effect of comonomer on the fastestcrystallization half-times of modified PCT copolyesters.

FIG. 2 is a graph showing the effect of comonomer on thebrittle-to-ductile transition temperature (T_(bd)) in a notched Izodimpact strength test ASTM D256, ⅛-in thick, 10-mil notch).

FIG. 3 is a graph showing the effect of2,2,4,4-tetramethyl-1,3-cyclobutanediol composition on the glasstransition temperature (Tg) of the copolyester.

DETAILED DESCRIPTION OF THE INVENTION

The present invention may be understood more readily by reference to thefollowing detailed description of certain embodiments of the inventionand the working examples. In accordance with the purpose(s) of thisinvention, certain embodiments of the invention are described in theSummary of the Invention and are further described herein below. Also,other embodiments of the invention are described herein.

It is believed that polyesters useful in the invention described hereincan have a combination of two or more physical properties such as highimpact strengths, moderate glass transition temperatures, chemicalresistance, hydrolytic stability, toughness, low ductile-to-brittletransition temperatures, good color and clarity, low densities, longcrystallization half-times, and good processability thereby easilypermitting them to be formed into articles. In some of the embodimentsof the invention, the polyesters have a unique combination of theproperties of good impact strength, heat resistance, chemicalresistance, density and/or the combination of the properties of goodimpact strength, heat resistance, and processability and/or thecombination of two or more of the described properties, that have neverbefore been believed to be present in a polyester.

The term “polyester”, as used herein, is intended to include“copolyesters” and is understood to mean a synthetic polymer prepared bythe reaction of one or more difunctional carboxylic acids and/ormultifunctional carboxylic acids with one or more difunctional hydroxylcompounds and/or multifunctional hydroxyl compounds. Typically thedifunctional carboxylic acid can be a dicarboxylic acid and thedifunctional hydroxyl compound can be a dihydric alcohol such as, forexample, glycols and diols. The term “glycol” as used in thisapplication includes, but is not limited to, diols, glycols, and/ormultifunctional hydroxyl compounds, for example, branching agents.Alternatively, the difunctional carboxylic acid may be a hydroxycarboxylic acid such as, for example, p-hydroxybenzoic acid, and thedifunctional hydroxyl compound may be an aromatic nucleus bearing 2hydroxyl substituents such as, for example, hydroquinone. The term“residue”, as used herein, means any organic structure incorporated intoa polymer through a polycondensation and/or an esterification reactionfrom the corresponding monomer. The term “repeating unit”, as usedherein, means an organic structure having a dicarboxylic acid residueand a diol residue bonded through a carbonyloxy group. Thus, forexample, the dicarboxylic acid residues may be derived from adicarboxylic acid monomer or its associated acid halides, esters, salts,anhydrides, or mixtures thereof. As used herein, therefore, the termdicarboxylic acid is intended to include dicarboxylic acids and anyderivative of a dicarboxylic acid, including its associated acidhalides, esters, half-esters, salts, half-salts, anhydrides, mixedanhydrides, or mixtures thereof, useful in a reaction process with adiol to make polyester. Furthermore, as used in this application, theterm “diacid” includes multifunctional acids, for example, branchingagents. As used herein, the term “terephthalic acid” is intended toinclude terephthalic acid itself and residues thereof as well as anyderivative of terephthalic acid, including its associated acid halides,esters, half-esters, salts, half-salts, anhydrides, mixed anhydrides, ormixtures thereof or residues thereof useful in a reaction process with adiol to make polyester.

In one embodiment, terephthalic acid may be used as the startingmaterial. In another embodiment, dimethyl terephthalate may be used asthe starting material. In yet another embodiment, mixtures ofterephthalic acid and dimethyl terephthalate may be used as the startingmaterial and/or as an intermediate material.

The polyesters used in the present invention typically can be preparedfrom dicarboxylic acids and diols which react in substantially equalproportions and are incorporated into the polyester polymer as theircorresponding residues. The polyesters of the present invention,therefore, can contain substantially equal molar proportions of acidresidues (100 mole %) and diol (and/or multifunctional hydroxylcompounds) residues (100 mole %) such that the total moles of repeatingunits is equal to 100 mole %. The mole percentages provided in thepresent disclosure, therefore, may be based on the total moles of acidresidues, the total moles of diol residues, or the total moles ofrepeating units. For example, a polyester containing 30 mole %isophthalic acid, based on the total acid residues, means the polyestercontains 30 mole % isophthalic acid residues out of a total of 100 mole% acid residues. Thus, there are 30 moles of isophthalic acid residuesamong every 100 moles of acid residues. In another example, a polyestercontaining 30 mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol, based onthe total diol residues, means the polyester contains 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues out of a total of 100mole % diol residues. Thus, there are 30 moles of2,2,4,4-tetramethyl-1,3-cyclobutanediol residues among every 100 molesof diol residues.

In other aspects of the invention, the Tg of the polyesters useful inthe invention can be at least one of the following ranges: 85 to 130°C.; 85 to 125° C.; 85 to 120° C.; 85 to 115° C.; 85 to 110° C.; 85 to105° C.; 85 to 100° C.; 85 to 95° C.; 85 to 90° C.; 90 to 130° C.; 90 to125° C.; 90 to 120° C.; 90 to 115° C.; 90 to 110° C.; 90 to 105° C.; 90to 100° C.; 90 to 95° C.; 95 to 130° C.; 95 to 125° C.; 95 to 120° C.;95 to 115° C.; 95 to 110° C.; 95 to 105° C.; 95 to 100° C.; 100 to 130°C.; 100 to 125° C.; 100 to 120° C.; 100 to 115° C.; 100 to 110° C.; 100to 105° C.; 105 to 130° C.; 105 to 125° C.; 105 to 120° C.; 105 to 115°C.; 105 to 110° C.; greater than 105 to 130° C.; greater than 105 to125° C.; greater than 105 to 120° C.; greater than 105 to 115° C.;greater than 105 to 110° C.; 110 to 130° C.; 110 to 125° C.; 110 to 120°C.; 110 to 115° C.; 115 to 130° C.; 115 to 125° C.; 115 to 120° C.; 115to 130° C.; 115 to 125° C.; 115 to 120° C.; 120 to 130° C.; and 125 to130° C.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 1 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 99 mole %1,4-cyclohexanedimethanol; 1 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 99 mole %1,4-cyclohexanedimethanol; 1 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 99 mole %1,4-cyclohexanedimethanol; 1 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 99 mole %1,4-cyclohexanedimethanol; 1 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 99 mole %1,4-cyclohexanedimethanol, 1 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 99 mole %1,4-cyclohexanedimethanol; 1 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 99 mole %1,4-cyclohexanedimethanol; 1 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 99 mole %1,4-cyclohexanedimethanol; 1 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 99 mole %1,4-cyclohexanedimethanol; 1 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 99 mole %1,4-cyclohexanedimethanol; 1 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 99 mole %1,4-cyclohexanedimethanol; 1 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 99 mole %1,4-cyclohexanedimethanol; 1 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 99 mole %1,4-cyclohexanedimethanol; 1 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 99 mole %1,4-cyclohexanedimethanol; 1 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 99 mole %1,4-cyclohexanedimethanol; 1 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 99 mole %1,4-cyclohexanedimethanol; 1 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 99 mole %1,4-cyclohexanedimethanol; 1 to 15 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 85 to 99 mole %1,4-cyclohexanedimethanol; 1 to 10 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 90 to 99 mole %1,4-cyclohexanedimethanol; and 1 to 5 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 95 to 99 mole %1,4-cyclohexanedimethanol; greater than 0.01 to 10 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 90 to less than 99.99 mole %1,4-cyclohexanedimethanol; and greater than 0.01 to 5 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 95 to less than 99.99 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the film or sheet of the invention include but arenot limited to at least one of the following combinations of ranges: 5to 99 mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 95 mole %1,4-cyclohexanedimethanol; 5 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 95 mole %1,4-cyclohexanedimethanol; 5 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 95 mole %1,4-cyclohexanedimethanol; 5 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 95 mole %1,4-cyclohexanedimethanol; 5 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 95 mole %1,4-cyclohexanedimethanol, 5 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 95 mole %1,4-cyclohexanedimethanol; 5 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 95 mole %1,4-cyclohexanedimethanol; 5 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 95 mole %1,4-cyclohexanedimethanol; 5 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 95 mole %1,4-cyclohexanedimethanol; 5 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 95 mole %1,4-cyclohexanedimethanol; and 5 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 95 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 5 to less than 50mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 50 to 95mole % 1,4-cyclohexanedimethanol; 5 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 95 mole %1,4-cyclohexanedimethanol; 5 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 95 mole %1,4-cyclohexanedimethanol; 5 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 95 mole %1,4-cyclohexanedimethanol; 5 to less than 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 65 to 95 mole %1,4-cyclohexanedimethanol; 5 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 95 mole %1,4-cyclohexanedimethanol; 5 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 95 mole %1,4-cyclohexanedimethanol; 5 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 95 mole %1,4-cyclohexanedimethanol; 5 to 15 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 85 to 95 mole %1,4-cyclohexanedimethanol; and 5 to 10 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 90 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the film or sheet of the invention include but arenot limited to at least one of the following combinations of ranges: 10to 99 mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 90 mole %1,4-cyclohexanedimethanol; 10 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 90 mole %1,4-cyclohexanedimethanol; 10 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 90 mole %1,4-cyclohexanedimethanol; 10 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 90 mole %1,4-cyclohexanedimethanol; 10 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 90 mole %1,4-cyclohexanedimethanol, 10 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 90 mole %1,4-cyclohexanedimethanol; 10 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 90 mole %1,4-cyclohexanedimethanol; 10 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 90 mole %1,4-cyclohexanedimethanol; 10 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 90 mole %1,4-cyclohexanedimethanol; 10 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 90 mole %1,4-cyclohexanedimethanol; and 10 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 90 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 10 to less than 50mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 50 to 90mole % 1,4-cyclohexanedimethanol; 10 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 90 mole %1,4-cyclohexanedimethanol; 10 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 90 mole %1,4-cyclohexanedimethanol; 10 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 90 mole %1,4-cyclohexanedimethanol; 10 to less than 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 65 up to 90mole % 1,4-cyclohexanedimethanol; 10 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 90 mole %1,4-cyclohexanedimethanol; 10 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 75 to 90 mole %1,4-cyclohexanedimethanol. 10 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 80 to 90 mole %1,4-cyclohexanedimethanol; and 10 to 15 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 85 to 90 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 11 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 89 mole %1,4-cyclohexanedimethanol; 11 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 89 mole %1,4-cyclohexanedimethanol; 11 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 89 mole %1,4-cyclohexanedimethanol; 11 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 89 mole %1,4-cyclohexanedimethanol; 11 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 89 mole %1,4-cyclohexanedimethanol, 11 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 89 mole %1,4-cyclohexanedimethanol; 11 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 89 mole %1,4-cyclohexanedimethanol; 11 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 89 mole %1,4-cyclohexanedimethanol; 11 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 89 mole %1,4-cyclohexanedimethanol; 11 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 89 mole %1,4-cyclohexanedimethanol; and 11 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 89 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 11 to less than 50mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 50 up to89 mole % 1,4-cyclohexanedimethanol; 11 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 89 mole %1,4-cyclohexanedimethanol; 11 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 89 mole %1,4-cyclohexanedimethanol; 11 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 89 mole %1,4-cyclohexanedimethanol; 11 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 89 mole %1,4-cyclohexanedimethanol; 11 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 89 mole %1,4-cyclohexanedimethanol; 11 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 89 mole %1,4-cyclohexanedimethanol, and 11 to 15 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 85 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 12 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 86 mole %1,4-cyclohexanedimethanol; 12 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 88 mole %1,4-cyclohexanedimethanol; 12 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 88 mole %1,4-cyclohexanedimethanol; 12 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 88 mole %1,4-cyclohexanedimethanol; 12 to 86 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 14 to 88 mole %1,4-cyclohexanedimethanol, 12 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 88 mole %1,4-cyclohexanedimethanol; 12 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 88 mole %1,4-cyclohexanedimethanol; 12 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 88 mole %1,4-cyclohexanedimethanol; 12 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 88 mole %1,4-cyclohexanedimethanol; 12 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 88 mole %1,4-cyclohexanedimethanol; and 12 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 88 mole %1,4-cyclohexanedimethanol;

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 12 to less than 50mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 50 up to88 mole % 1,4-cyclohexanedimethanol; 12 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 88 mole %1,4-cyclohexanedimethanol; 12 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 88 mole %1,4-cyclohexanedimethanol; 12 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 88 mole %1,4-cyclohexanedimethanol; 12 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 88 mole %1,4-cyclohexanedimethanol; 12 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 88 mole %1,4-cyclohexanedimethanol; 12 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 88 mole %1,4-cyclohexanedimethanol, and 12 to 15 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol; and 85 to 88 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 13 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 87 mole %1,4-cyclohexanedimethanol; 13 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 87 mole %1,4-cyclohexanedimethanol; 13 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 87 mole %1,4-cyclohexanedimethanol; 13 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 87 mole %1,4-cyclohexanedimethanol; 13 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 87 mole %1,4-cyclohexanedimethanol, 13 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 87 mole %1,4-cyclohexanedimethanol; 13 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 87 mole %1,4-cyclohexanedimethanol; 13 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 87 mole %1,4-cyclohexanedimethanol; 13 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 87 mole %1,4-cyclohexanedimethanol; 13 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 87 mole %1,4-cyclohexanedimethanol; and 13 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 87 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 13 to less than 50mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 50 up to87 mole % 1,4-cyclohexanedimethanol; 13 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 87 mole %1,4-cyclohexanedimethanol; 13 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 87 mole %1,4-cyclohexanedimethanol; 13 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 87 mole %1,4-cyclohexanedimethanol; 13 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 87 mole %1,4-cyclohexanedimethanol; 13 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 87 mole %1,4-cyclohexanedimethanol; 13 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 87 mole %1,4-cyclohexanedimethanol, and 13 to 15 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol; and 85 to 87 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 14 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 86 mole %1,4-cyclohexanedimethanol; 14 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 86 mole %1,4-cyclohexanedimethanol; 14 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 86 mole %1,4-cyclohexanedimethanol; 14 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 86 mole %1,4-cyclohexanedimethanol; 14 to 86 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 14 to 86 mole %1,4-cyclohexanedimethanol, 14 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 86 mole %1,4-cyclohexanedimethanol; 14 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 86 mole %1,4-cyclohexanedimethanol; 14 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 86 mole %1,4-cyclohexanedimethanol; 14 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 86 mole %1,4-cyclohexanedimethanol; 14 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 86 mole %1,4-cyclohexanedimethanol; and 14 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 86 mole %1,4-cyclohexanedimethanol;

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 14 to less than 50mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 50 up to86 mole % 1,4-cyclohexanedimethanol; 14 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 86 mole %1,4-cyclohexanedimethanol; 14 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 86 mole %1,4-cyclohexanedimethanol; 14 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 86 mole %1,4-cyclohexanedimethanol; 14 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 86 mole %1,4-cyclohexanedimethanol; 14 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 86 mole %1,4-cyclohexanedimethanol; and 14 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 86 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 15 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 85 mole %1,4-cyclohexanedimethanol; 15 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 85 mole %1,4-cyclohexanedimethanol; 15 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 85 mole %1,4-cyclohexanedimethanol; 15 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 85 mole %1,4-cyclohexanedimethanol; 15 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 85 mole %1,4-cyclohexanedimethanol, 15 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 85 mole %1,4-cyclohexanedimethanol; 15 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 85 mole %1,4-cyclohexanedimethanol; 15 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 85 mole %1,4-cyclohexanedimethanol; 15 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 85 mole %1,4-cyclohexanedimethanol; 15 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 85 mole %1,4-cyclohexanedimethanol; and 15 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 85 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 15 to less than 50mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 50 up to85 mole % 1,4-cyclohexanedimethanol; 15 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 85 mole %1,4-cyclohexanedimethanol; 15 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 85 mole %1,4-cyclohexanedimethanol; 15 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 85 mole %1,4-cyclohexanedimethanol; 15 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 85 mole %1,4-cyclohexanedimethanol; 15 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 85 mole %1,4-cyclohexanedimethanol; 15 to 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 80 to 85 mole %1,4-cyclohexanedimethanol; and 17 to 23 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 77 to 83 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 20 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 80 mole %1,4-cyclohexanedimethanol; 20 to 95 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 5 to 80 mole %1,4-cyclohexanedimethanol; 20 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 80 mole %1,4-cyclohexanedimethanol; 20 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 80 mole %1,4-cyclohexanedimethanol; 20 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 80 mole %1,4-cyclohexanedimethanol, 20 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 80 mole %1,4-cyclohexanedimethanol; 20 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 80 mole %1,4-cyclohexanedimethanol; 20 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 80 mole %1,4-cyclohexanedimethanol; 20 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 80 mole %1,4-cyclohexanedimethanol; 20 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 80 mole %1,4-cyclohexanedimethanol; 20 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 80 mole %1,4-cyclohexanedimethanol; 20 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 80 mole %1,4-cyclohexanedimethanol; 20 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 80 mole %1,4-cyclohexanedimethanol; 20 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 80 mole %1,4-cyclohexanedimethanol; 20 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 80 mole %1,4-cyclohexanedimethanol; and 20 to 25 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 75 to 80 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 25 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to 75 mole %1,4-cyclohexanedimethanol; 25 to 90 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 10 to 75 mole %1,4-cyclohexanedimethanol; 25 to 85 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 15 to 75 mole %1,4-cyclohexanedimethanol; 25 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 75 mole %1,4-cyclohexanedimethanol, 25 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 75 mole %1,4-cyclohexanedimethanol; 25 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 75 mole %1,4-cyclohexanedimethanol; 25 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 75 mole %1,4-cyclohexanedimethanol; 25 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 75 mole %1,4-cyclohexanedimethanol; 25 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 75 mole %1,4-cyclohexanedimethanol; 25 to 50 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 50 to 75 mole %1,4-cyclohexanedimethanol; 25 to 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 55 to 75 mole %1,4-cyclohexanedimethanol; 25 to 40 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 60 to 75 mole %1,4-cyclohexanedimethanol; 25 to 35 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 65 to 75 mole %1,4-cyclohexanedimethanol; 25 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 70 to 75 mole %1,4-cyclohexanedimethanol.

In other aspects of the invention, the glycol component for thepolyesters useful in the invention include but are not limited to atleast one of the following combinations of ranges: 35 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 65 mole %1,4-cyclohexanedimethanol; 37 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 63 mole %1,4-cyclohexanedimethanol; 40 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 60 mole %1,4-cyclohexanedimethanol; 45 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 55 mole %1,4-cyclohexanedimethanol; 50 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 50 mole %1,4-cyclohexanedimethanol; greater than 50 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to less than 50 mole %1,4-cyclohexanedimethanol; 55 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 45 mole %1,4-cyclohexanedimethanol; 60 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 40 mole %1,4-cyclohexanedimethanol; 65 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 35 mole %1,4-cyclohexanedimethanol; 70 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to 30 mole %1,4-cyclohexanedimethanol; 40 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 60 mole %1,4-cyclohexanedimethanol; 45 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 55 mole %1,4-cyclohexanedimethanol; 50 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 50 mole %1,4-cyclohexanedimethanol; 55 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 45 mole %1,4-cyclohexanedimethanol; 60 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 40 mole %1,4-cyclohexanedimethanol; 65 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to 35 mole %1,4-cyclohexanedimethanol; 40 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 60 mole %1,4-cyclohexanedimethanol; 45 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 55 mole %1,4-cyclohexanedimethanol; 50 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 50 mole %1,4-cyclohexanedimethanol; greater than 50 to 99 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 1 to less than 50 mole %1,4-cyclohexanedimethanol; greater than 50 to 80 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 20 to less than 50 mole %1,4-cyclohexanedimethanol; greater than 50 to 75 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 25 to less than 50 mole %1,4-cyclohexanedimethanol; greater than 50 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to less than 50 mole %1,4-cyclohexanedimethanol; 55 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 45 mole %1,4-cyclohexanedimethanol; 60 to 70 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 30 to 40 mole %1,4-cyclohexanedimethanol; 40 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 60 mole %1,4-cyclohexanedimethanol; 40 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 60 mole %1,4-cyclohexanedimethanol; 40 to less than 45 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and greater than 55 to 60 mole %1,4-cyclohexanedimethanol; 45 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 55 mole %1,4-cyclohexanedimethanol; greater than 50 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to less than 50 mole %1,4-cyclohexanedimethanol; 50 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 50 mole %1,4-cyclohexanedimethanol; 55 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 45 mole %1,4-cyclohexanedimethanol; 40 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 60 mole %1,4-cyclohexanedimethanol; 45 to 60 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 40 to 55 mole %1,4-cyclohexanedimethanol; 45 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 55 mole %1,4-cyclohexanedimethanol; greater than 45 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol; 45 to less than 55 mole %1,4-cyclohexanedimethanol; and 46 to 55 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 45 to 54 mole %1,4-cyclohexanedimethanol; and 46 to 65 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol and 35 to 54 mole %1,4-cyclohexanedimethanol.

In addition to the diols set forth above, the polyesters useful in thepolyester compositions of the invention may also be made from1,3-propanediol, 1,4-butanediol, or mixtures thereof.

In addition to the diols set forth above, the polyesters useful in thepolyester compositions of the invention may also be made from1,3-propanediol, 1,4-butanediol, or mixtures thereof can possess atleast one of the Tg ranges described herein, at least one of theinherent viscosity ranges described herein, and/or at least one of theglycol or diacid ranges described herein. In addition or in thealternative, the polyesters useful in the invention can be made from1,3-propanediol or 1,4-butanediol or mixtures thereof may also be madefrom 1,4-cyclohexaned methanol in at least one of the following amounts:from 0.1 to 99 mole %; from 0.1 to 95 mole %; from 0.1 to 90 mole %;from 0.1 to 85 mole %; from 0.1 to 80 mole %; from 0.1 to 70 mole %;from 0.1 to 60 mole %; from 0.1 to 50 mole %; from 0.1 to 40 mole %;from 0.1 to 35 mole %; from 0.1 to 30 mole %; from 0.1 to 25 mole %;from 0.1 to 20 mole %; from 0.1 to 15 mole %; from 0.1 to 10 mole %;from 0.1 to 5 mole %; from 1 to 99 mole %; 1 to 95 mole %; from 1 to 90mole %; from 1 to 85 mole %; from 1 to 80 mole %; from 1 to 70 mole %;from 1 to 60 mole %; from 1 to 50 mole %; from 1 to 40 mole %; from 1 to35 mole %; from 1 to 30 mole %; from 1 to 25 mole %; from 1 to 20 mole%; from 1 to 15 mole %; from 1 to 10 mole %; from 1 to 5 mole %; 5 to 99mole %; 5 to 95 mole %; from 5 to 90 mole %; from 5 to 85 mole %; from 5to 80 mole %; 5 to 70 mole %; from 5 to 60 mole %; from 5 to 50 mole %;from 5 to 40 mole %; from 5 to 35 mole %; from 5 to 30 mole %; from 5 to25 mole %; from 5 to 20 mole %; and from 5 to 15 mole %; from 5 to 10mole %; from 10 to 99 mole %; 10 to 95 mole %; from 10 to 90 mole %;from 10 to 85 mole %; from 10 to 80 mole %; from 10 to 70 mole %; from10 to 60 mole %; from 10 to 50 mole %; from 10 to 40 mole %; from 10 to35 mole %; from 10 to 30 mole %; from 10 to 25 mole %; from 10 to 20mole %; from 10 to 15 mole %; from 20 to 99 mole %; 20 to 95 mole %;from 20 to 90 mole %; from 20 to 85 mole %; from 20 to 80 mole %; from20 to 70 mole %; from 20 to 60 mole %; from 20 to 50 mole %; from 20 to40 mole %; from 20 to 35 mole %; from 20 to 30 mole %; and from 20 to 25mole %.

For certain embodiments of the invention, the polyesters useful in theinvention may exhibit at least one of the following inherent viscositiesas determined in 60/40 (wt/wt) phenol/tetrachloroethane at aconcentration of 0.5 g/100 ml at 25° C.: 0.10 to 1.2 dL/g; 0.10 to 1.1dL/g; 0.10 to 1 dL/g; 0.10 to less than 1 dL/g; 0.10 to 0.98 dL/g; 0.10to 0.95 dL/g; 0.10 to 0.90 dL/g; 0.10 to 0.85 dL/g; 0.10 to 0.80 dL/g;0.10 to 0.75 dL/g; 0.10 to less than 0.75 dL/g; 0.10 to 0.72 dL/g; 0.10to 0.70 dL/g; 0.10 to less than 0.70 dL/g; 0.10 to 0.68 dL/g; 0.10 toless than 0.68 dL/g; 0.10 to 0.65 dL/g; 0.20 to 1.2 dL/g; 0.20 to 1.1dL/g; 0.20 to 1 dL/g; 0.20 to less than 1 dL/g; 0.20 to 0.98 dL/g; 0.20to 0.95 dL/g; 0.20 to 0.90 dL/g; 0.20 to 0.85 dL/g; 0.20 to 0.80 dL/g;0.20 to 0.75 dL/g; 0.20 to less than 0.75 dL/g; 0.20 to 0.72 dL/g; 0.20to 0.70 dL/g; 0.20 to less than 0.70 dL/g; 0.20 to 0.68 dL/g; 0.20 toless than 0.68 dL/g; 0.20 to 0.65 dL/g; 0.35 to 1.2 dL/g; 0.35 to 1.1dL/g; 0.35 to 1 dL/g; 0.35 to less than 1 dL/g; 0.35 to 0.98 dL/g; 0.35to 0.95 dL/g; 0.35 to 0.90 dL/g; 0.35 to 0.85 dL/g; 0.35 to 0.80 dL/g;0.35 to 0.75 dL/g; 0.35 to less than 0.75 dL/g; 0.35 to 0.72 dL/g; 0.35to 0.70 dL/g; 0.35 to less than 0.70 dL/g; 0.35 to 0.68 dL/g; 0.35 toless than 0.68 dL/g; 0.35 to 0.65 dL/g; 0.40 to 1.2 dL/g; 0.40 to 1.1dL/g; 0.40 to 1 dL/g; 0.40 to less than 1 dL/g; 0.40 to 0.98 dL/g; 0.40to 0.95 dL/g; 0.40 to 0.90 dL/g; 0.40 to 0.85 dL/g; 0.40 to 0.80 dL/g;0.40 to 0.75 dL/g; 0.40 to less than 0.75 dL/g; 0.40 to 0.72 dL/g; 0.40to 0.70 dL/g; 0.40 to less than 0.70 dL/g; 0.40 to 0.68 dL/g; 0.40 toless than 0.68 dL/g; 0.40 to 0.65 dL/g; greater than 0.42 to 1.2 dL/g;greater than 0.42 to 1.1 dL/g; greater than 0.42 to 1 dL/g; greater than0.42 to less than 1 dL/g; greater than 0.42 to 0.98 dL/g; greater than0.42 to 0.95 dL/g; greater than 0.42 to 0.90 dL/g; greater than 0.42 to0.85 dL/g; greater than 0.42 to 0.80 dL/g; greater than 0.42 to 0.75dL/g; greater than 0.42 to less than 0.75 dL/g; greater than 0.42 to0.72 dL/g; greater than 0.42 to less than 0.70 dL/g; greater than 0.42to 0.68 dL/g; greater than 0.42 to less than 0.68 dL/g; and greater than0.42 to 0.65 dL/g.

For certain embodiments of the invention, the polyesters useful in theinvention may exhibit at least one of the following inherent viscositiesas determined in 60/40 (wt/wt) phenol/tetrachloroethane at aconcentration of 0.5 g/100 ml at 25° C.: 0.45 to 1.2 dL/g; 0.45 to 1.1dL/g; 0.45 to 1 dL/g; 0.45 to 0.98 dL/g; 0.45 to 0.95 dL/g; 0.45 to 0.90dL/g; 0.45 to 0.85 dL/g; 0.45 to 0.80 dL/g; 0.45 to 0.75 dL/g; 0.45 toless than 0.75 dL/g; 0.45 to 0.72 dL/g; 0.45 to 0.70 dL/g; 0.45 to lessthan 0.70 dL/g; 0.45 to 0.68 dL/g; 0.45 to less than 0.68 dL/g; 0.45 to0.65 dL/g; 0.50 to 1.2 dL/g; 0.50 to 1.1 dL/g; 0.50 to 1 dL/g; 0.50 toless than 1 dL/g; 0.50 to 0.98 dL/g; 0.50 to 0.95 dL/g; 0.50 to 0.90dL/g; 0.50 to 0.85 dL/g; 0.50 to 0.80 dL/g; 0.50 to 0.75 dL/g; 0.50 toless than 0.75 dL/g; 0.50 to 0.72 dL/g; 0.50 to 0.70 dL/g; 0.50 to lessthan 0.70 dL/g; 0.50 to 0.68 dL/g; 0.50 to less than 0.68 dL/g; 0.50 to0.65 dL/g; 0.55 to 1.2 dL/g; 0.55 to 1.1 dL/g; 0.55 to 1 dL/g; 0.55 toless than 1 dL/g; 0.55 to 0.98 dL/g; 0.55 to 0.95 dL/g; 0.55 to 0.90dL/g; 0.55 to 0.85 dL/g; 0.55 to 0.80 dL/g; 0.55 to 0.75 dL/g; 0.55 toless than 0.75 dL/g; 0.55 to 0.72 dL/g; 0.55 to 0.70 dL/g; 0.55 to lessthan 0.70 dL/g; 0.55 to 0.68 dL/g; 0.55 to less than 0.68 dL/g; 0.55 to0.65 dL/g; 0.58 to 1.2 dL/g; 0.58 to 1.1 dL/g; 0.58 to 1 dL/g; 0.58 toless than 1 dL/g; 0.58 to 0.98 dL/g; 0.58 to 0.95 dL/g; 0.58 to 0.90dL/g; 0.58 to 0.85 dL/g; 0.58 to 0.80 dL/g; 0.58 to 0.75 dL/g; 0.58 toless than 0.75 dL/g; 0.58 to 0.72 dL/g; 0.58 to 0.70 dL/g; 0.58 to lessthan 0.70 dL/g; 0.58 to 0.68 dL/g; 0.58 to less than 0.68 dL/g; 0.58 to0.65 dL/g; 0.60 to 1.2 dL/g; 0.60 to 1.1 dL/g; 0.60 to 1 dL/g; 0.60 toless than 1 dL/g; 0.60 to 0.98 dL/g; 0.60 to 0.95 dL/g; 0.60 to 0.90dL/g; 0.60 to 0.85 dL/g; 0.60 to 0.80 dL/g; 0.60 to 0.75 dL/g; 0.60 toless than 0.75 dL/g; 0.60 to 0.72 dL/g; 0.60 to 0.70 dL/g; 0.60 to lessthan 0.70 dL/g; 0.60 to 0.68 dL/g; 0.60 to less than 0.68 dL/g; 0.60 to0.65 dL/g; 0.65 to 1.2 dL/g; 0.65 to 1.1 dL/g; 0.65 to 1 dL/g; 0.65 toless than 1 dL/g; 0.65 to 0.98 dL/g; 0.65 to 0.95 dL/g; 0.65 to 0.90dL/g; 0.65 to 0.85 dL/g; 0.65 to 0.80 dL/g; 0.65 to 0.75 dL/g; 0.65 toless than 0.75 dL/g; 0.65 to 0.72 dL/g; 0.65 to 0.70 dL/g; 0.65 to lessthan 0.70 dL/g; 0.68 to 1.2 dL/g; 0.68 to 1.1 dL/g; 0.68 to 1 dL/g; 0.68to less than 1 dL/g; 0.68 to 0.98 dL/g; 0.68 to 0.95 dL/g; 0.68 to 0.90dL/g; 0.68 to 0.85 dL/g; 0.68 to 0.80 dL/g; 0.68 to 0.75 dL/g; 0.68 toless than 0.75 dL/g; 0.68 to 0.72 dL/g; greater than 0.76 dL/g to 1.2dL/g; greater than 0.76 dL/g to 1.1 dL/g; greater than 0.76 dL/g to 1dL/g; greater than 0.76 dL/g to less than 1 dL/g; greater than 0.76 dL/gto 0.98 dL/g; greater than 0.76 dL/g to 0.95 dL/g; greater than 0.76dL/g to 0.90 dL/g; greater than 0.80 dL/g to 1.2 dL/g; greater than 0.80dL/g to 1.1 dL/g; greater than 0.80 dL/g to 1 dL/g; greater than 0.80dL/g to less than 1 dL/g; greater than 0.80 dL/g to 1.2 dL/g; greaterthan 0.80 dL/g to 0.98 dL/g; greater than 0.80 dL/g to 0.95 dL/g;greater than 0.80 dL/g to 0.90 dL/g.

It is contemplated that the polyester compositions of the invention canpossess at least one of the inherent viscosity ranges described hereinand at least one of the monomer ranges for the compositions describedherein unless otherwise stated. It is also contemplated that thepolyester compositions of the invention can posses at least one of theTg ranges described herein and at least one of the monomer ranges forthe compositions described herein unless otherwise stated. It is alsocontemplated that the polyester compositions of the invention can possesat least one of the Tg ranges described herein, at least one of theinherent viscosity ranges described herein, and at least one of themonomer ranges for the compositions described herein unless otherwisestated.

For the desired polyester, the molar ratio of cis/trans2,2,4,4-tetramethyl-1,3-cyclobutanediol can vary from the pure form ofeach or mixtures thereof. In certain embodiments, the molar percentagesfor cis and/or trans 2,2,4,4-tetramethyl-1,3-cyclobutanediol are greaterthan 50 mole % cis and less than 50 mole % trans; or greater than 55mole % cis and less than 45 mole % trans; or 30 to 70 mole % cis and 70to 30% trans; or 40 to 60 mole % cis and 60 to 40 mole % trans; or 50 to70 mole % trans and 50 to 30 mole % cis; or 50 to 70 mole % cis and 50to 30% trans or 60 to 70 mole % cis and 30 to 40 mole % trans; orgreater than 70 mole % cis and less than 30 mole % trans; wherein thetotal sum of the mole percentages for cis- andtrans-2,2,4,4-tetramethyl-1,3-cyclobutanediol is equal to 100 mole %.The molar ratio of cis/trans 1,4-cyclohexandimethanol can vary withinthe range of 50/50 to 0/100, for example, between 40/60 to 20/80.

In certain embodiments, terephthalic acid, or an ester thereof, such as,for example, dimethyl terephthalate, or a mixture of terephthalic acidand an ester thereof, makes up most or all of the dicarboxylic acidcomponent used to form the polyesters useful in the invention. Incertain embodiments, terephthalic acid residues can make up a portion orall of the dicarboxylic acid component used to form the presentpolyester at a concentration of at least 70 mole %, such as at least 80mole %, at least 90 mole %, at least 95 mole %, at least 99 mole %, or100 mole %. In certain embodiments, polyesters with higher amounts ofterephthalic acid can be used in order to produce higher impact strengthproperties. For purposes of this disclosure, the terms “terephthalicacid” and “dimethyl terephthalate are used interchangeably herein. Inone embodiment, dimethyl terephthalate is part or all of thedicarboxylic acid component used to make the polyesters useful in thepresent invention. In all embodiments, ranges of from 70 to 100 mole %;or 80 to 100 mole %; or 90 to 100 mole %; or 99 to 100 mole %; or 100mole % terephthalic acid and/or dimethyl terephthalate and/or mixturesthereof may be used.

In addition to terephthalic acid residues, the dicarboxylic acidcomponent of the polyesters useful in the invention can comprise up to30 mole %, up to 20 mole %, up to 10 mole %, up to 5 mole %, or up to 1mole % of one or more modifying aromatic dicarboxylic acids. Yet anotherembodiment contains 0 mole % modifying aromatic dicarboxylic acids.Thus, if present, it is contemplated that the amount of one or moremodifying aromatic dicarboxylic acids can range from any of thesepreceding endpoint values including, for example, from 0.01 to 30 mole%, from 0.01 to 20 mole %, from 0.01 to 10 mole %, from 0.01 to 5 mole%, or from 0.01 to 1 mole % of one or more modifying aromaticdicarboxylic acids. In one embodiment, modifying aromatic dicarboxylicacids that may be used in the present invention include but are notlimited to those having up to 20 carbon atoms, and that can be linear,para-oriented, or symmetrical. Examples of modifying aromaticdicarboxylic acids which may be used in this invention include, but arenot limited to, isophthalic acid, 4,4′-biphenyldicarboxylic acid, 1,4-,1,5-, 2,6-, 2,7-naphthalenedicarboxylic acid, andtrans-4,4′-stilbenedicarboxylic acid, and esters thereof. In oneembodiment, isophthalic acid is the modifying aromatic dicarboxylicacid.

The carboxylic acid component of the polyesters useful in the inventioncan be further modified with up to 10 mole %, such as up to 5 mole % orup to 1 mole % of one or more aliphatic dicarboxylic acids containing2-16 carbon atoms, such as, for example, malonic, succinic, glutaric,adipic, pimelic, suberic, azelaic and dodecanedioic dicarboxylic acids.Certain embodiments can also comprise 0.01 or more mole %, such as 0.1or more mole %, 1 or more mole %, 5 or more mole %, or 10 or more mole %of one or more modifying aliphatic dicarboxylic acids. Yet anotherembodiment contains 0 mole % modifying aliphatic dicarboxylic acids.Thus, if present, it is contemplated that the amount of one or moremodifying aliphatic dicarboxylic acids can range from any of thesepreceding endpoint values including, for example, from 0.01 to 10 mole %and from 0.1 to 10 mole %. The total mole % of the dicarboxylic acidcomponent is 100 mole %.

Esters of terephthalic acid and the other modifying dicarboxylic acidsor their corresponding esters and/or salts may be used instead of thedicarboxylic acids. Suitable examples of dicarboxylic acid estersinclude, but are not limited to, the dimethyl, diethyl, dipropyl,diisopropyl, dibutyl, and diphenyl esters. In one embodiment, the estersare chosen from at least one of the following: methyl, ethyl, propyl,isopropyl, and phenyl esters.

The 1,4-cyclohexanedimethanol may be cis, trans, or a mixture thereof,for example, a cis/trans ratio of 60:40 to 40:60. In another embodiment,the trans-1,4-cyclohexanedimethanol can be present in the amount of 60to 80 mole %.

The glycol component of the polyester portion of the polyestercompositions useful in the invention can contain 25 mole % or less ofone or more modifying glycols which are not2,2,4,4-tetramethyl-1,3-cyclobutanediol or 1,4-cyclohexanedimethanol; inone embodiment, the polyesters useful in the invention can contain lessthan 15 mole % of one or more modifying glycols. In another embodiment,the polyesters useful in the invention can contain 10 mole % or less ofone or more modifying glycols. In another embodiment, the polyestersuseful in the invention can contain 5 mole % or less of one or moremodifying glycols. In another embodiment, the polyesters useful in theinvention can contain 3 mole % or less of one or more modifying glycols.In another embodiment, the polyesters useful in the invention maycontain 0 mole % modifying glycols. Certain embodiments can also contain0.01 or more mole %, such as 0.1 or more mole %, 1 or more mole %, 5 ormore mole %, or 10 or more mole % of one or more modifying glycols.Thus, if present, it is contemplated that the amount of one or moremodifying glycols can range from any of these preceding endpoint valuesincluding, for example, from 0.01 to 15 mole % and from 0.1 to 10 mole%.

Modifying glycols useful in the polyesters useful in the invention referto diols other than 2,2,4,4,-tetramethyl-1,3-cyclobutanediol and1,4-cyclohexanedimethanol and may contain 2 to 16 carbon atoms. Examplesof suitable modifying glycols include, but are not limited to, ethyleneglycol, diethylene glycol, 1,2-propanediol, 1,3-propanediol, neopentylglycol, 1,4-butanediol, 1,5-pentanediol, 1,6-hexanediol, p-xylene glycolor mixtures thereof. In one embodiment, the modifying glycol is ethyleneglycol. In another embodiment, the modifying glycols include but are notlimited to 1,3-propanediol and/or 1,4-butanediol. In another embodiment,ethylene glycol is excluded as a modifying diol. In another embodiment,1,3-propanediol and 1,4-butanediol are excluded as modifying diols. Inanother embodiment, 2,2-dimethyl-1,3-propanediol is excluded as amodifying diol. The polyesters and/or the polycarbonates useful in thepolyesters compositions of the invention can comprise from 0 to 10 molepercent, for example, from 0.01 to 5 mole percent, from 0.01 to 1 molepercent, from 0.05 to 5 mole percent, from 0.05 to 1 mole percent, orfrom 0.1 to 0.7 mole percent, or 0.1 to 0.5 mole percent, based thetotal mole percentages of either the diol or diacid residues;respectively, of one or more residues of a branching monomer, alsoreferred to herein as a branching agent, having 3 or more carboxylsubstituents, hydroxyl substituents, or a combination thereof. Incertain embodiments, the branching monomer or agent may be added priorto and/or during and/or after the polymerization of the polyester. Thepolyester(s) useful in the invention can thus be linear or branched. Thepolycarbonate can also be linear or branched. In certain embodiments,the branching monomer or agent may be added prior to and/or duringand/or after the polymerization of the polycarbonate.

Examples of branching monomers include, but are not limited to,multifunctional acids or multifunctional alcohols such as trimelliticacid, trimellitic anhydride, pyromellitic dianhydride,trimethylolpropane, glycerol, pentaerythritol, citric acid, tartaricacid, 3-hydroxyglutaric acid and the like. In one embodiment, thebranching monomer residues can comprise 0.1 to 0.7 mole percent of oneor more residues chosen from at least one of the following: trimelliticanhydride, pyromellitic dianhydride, glycerol, sorbitol,1,2,6-hexanetriol, pentaerythritol, trimethylolethane, and/or trimesicacid. The branching monomer may be added to the polyester reactionmixture or blended with the polyester in the form of a concentrate asdescribed, for example, in U.S. Pat. Nos. 5,654,347 and 5,696,176, whosedisclosure regarding branching monomers is incorporated herein byreference.

The glass transition temperature (Tg) of the polyesters useful in theinvention was determined using a TA DSC 2920 from Thermal AnalystInstrument at a scan rate of 20° C./min.

Because of the long crystallization half-times (e.g., greater than 5minutes) at 170° C. exhibited by certain polyesters useful in thepresent invention, it can be possible to produce articles, including butnot limited to, injection molded parts, injection blow molded articles,injection stretch blow molded articles, extruded film, extruded sheet,extrusion blow molded articles, extrusion stretch blow molded articles,and fibers. The polyesters of the invention can be amorphous orsemicrystalline. In one aspect, certain polyesters useful in theinvention can have relatively low crystallinity. Certain polyestersuseful in the invention can thus have a substantially amorphousmorphology, meaning that the polyesters comprise substantially unorderedregions of polymer.

In one embodiment, an “amorphous” polyester can have a crystallizationhalf-time of greater than 5 minutes at 170° C. or greater than 10minutes at 170° C. or greater than 50 minutes at 170° C. or greater than100 minutes at 170° C. In one embodiment, of the invention, thecrystallization half-times are greater than 1,000 minutes at 170° C. Inanother embodiment of the invention, the crystallization half-times ofthe polyesters useful in the invention are greater than 10,000 minutesat 170° C. The crystallization half time of the polyesters, as usedherein, may be measured using methods well-known to persons of skill inthe art. For example, the crystallization half time of the polyester,t_(1/2), can be determined by measuring the light transmission of asample via a laser and photo detector as a function of time on atemperature controlled hot stage. This measurement can be done byexposing the polymers to a temperature, T_(max), and then cooling it tothe desired temperature. The sample can then be held at the desiredtemperature by a hot stage while transmission measurements were made asa function of time. Initially, the sample can be visually clear withhigh light transmission, and becomes opaque as the sample crystallizes.The crystallization half-time is the time at which the lighttransmission is halfway between the initial transmission and the finaltransmission. T_(max) is defined as the temperature required to melt thecrystalline domains of the sample (if crystalline domains are present).The sample can be heated to Tmax to condition the sample prior tocrystallization half time measurement. The absolute Tmax temperature isdifferent for each composition. For example PCT can be heated to sometemperature greater than 290° C. to melt the crystalline domains.

As shown in Table 1 and FIG. 1 of the Examples,2,2,4,4-tetramethyl-1,3-cyclobutanediol is more effective than othercomonomers such ethylene glycol and isophthalic acid at increasing thecrystallization half-time, i.e., the time required for a polymer toreach half of its maximum crystallinity. By decreasing thecrystallization rate of PCT, i.e. increasing the crystallizationhalf-time, amorphous articles based on modified PCT may be fabricated bymethods known in the art such as extrusion, injection molding, and thelike. As shown in Table 1, these materials can exhibit higher glasstransition temperatures and lower densities than other modified PCTcopolyesters.

The polyesters of the invention can exhibit an improvement in toughnesscombined with processability for some of the embodiments of theinvention. For example, it is unexpected that lowering the inherentviscosity slightly of the polyesters useful in the invention results ina more processable melt viscosity while retaining good physicalproperties of the polyesters such as toughness and heat resistance.

Increasing the content of 1,4-cyclohexanedimethanol in a copolyesterbased on terephthalic acid, ethylene glycol, and1,4-cyclohexanedimethanol can improve toughness can be determined by thebrittle-to-ductile transition temperature in a notched Izod impactstrength test as measured by ASTM D256. This toughness improvement, bylowering of the brittle-to-ductile transition temperature with1,4-cyclohexanedimethanol, is believed to occur due to the flexibilityand conformational behavior of 1,4-cyclohexanedimethanol in thecopolyester. Incorporating 2,2,4,4-tetramethyl-1,3-cyclobutanediol intoPCT is believed to improve toughness, by lowering the brittle-to-ductiletransition temperature, as shown in Table 2 and FIG. 2 of the Examples.This is unexpected given the rigidity of2,2,4,4-tetramethyl-1,3-cyclobutanediol.

In one embodiment, the melt viscosity of the polyester(s) useful in theinvention is less than 30,000 poise as measured a 1 radian/second on arotary melt rheometer at 290° C. In another embodiment, the meltviscosity of the polyester(s) useful in the invention is less than20,000 poise as measured a 1 radian/second on a rotary melt rheometer at290° C.

In one embodiment, the melt viscosity of the polyester(s) useful in theinvention is less than 15,000 poise as measured at 1 radian/second(rad/sec) on a rotary melt rheometer at 290° C. In one embodiment, themelt viscosity of the polyester(s) useful in the invention is less than10,000 poise as measured at 1 radian/second (rad/sec) on a rotary meltrheometer at 290° C. In another embodiment, the melt viscosity of thepolyester(s) useful in the invention is less than 6,000 poise asmeasured at 1 radian/second on a rotary melt rheometer at 290° C.Viscosity at rad/sec is related to processability. Typical polymers haveviscosities of less than 10,000 poise as measured at 1 radian/secondwhen measured at their processing temperature. Polyesters are typicallynot processed above 290° C. Polycarbonate is typically processed at 290°C. The viscosity at 1 rad/sec of a typical 12 melt flow ratepolycarbonate is 7000 poise at 290° C.

In one embodiment, polyesters of this invention exhibit superior notchedtoughness in thick sections. Notched Izod impact strength, as describedin ASTM D256, is a common method of measuring toughness. In oneembodiment, the polyesters useful in the invention exhibit a impactstrength of at least 150 J/m (3 ft-lb/in) at 23° C. with a 10-mil notchin a 3.2 mm (⅛-inch) thick bar determined according to ASTM D256; in oneembodiment, the polyesters useful in the invention exhibit a notchedIzod impact strength of at least (400 J/m) 7.5 ft-lb/in at 23° C. with a10-mil notch in a 3.2 mm (⅛-inch) thick bar determined according to ASTMD256; in one embodiment, the polyesters useful in the invention exhibita notched Izod impact strength of at least 10 ft-lb/in at 23° C. with a10-mil notch in a ⅛-inch thick bar determined according to ASTM D256; inone embodiment, the polyesters useful in the invention exhibit a notchedIzod impact strength of at least 1000 J/m (18 ft-lb/in) at 23° C. with a10-mil notch in a 3.2 mm (⅛-inch) thick bar determined according to ASTMD256. In one embodiment, the polyesters useful in the invention exhibita notched Izod impact strength of at least 150 J/m (3 ft-lb/in) at 23°C. with a 10-mil notch in a 6.4 mm (¼-inch) thick bar determinedaccording to ASTM D256; in one embodiment, the polyesters useful in theinvention exhibit a notched Izod impact strength of at least (400 J/M)7.5 ft-lb/in at 23° C. with a 10-mil notch in a 6.4 mm (¼-inch) thickbar determined according to ASTM D256; in one embodiment, the polyestersuseful in the invention exhibit a notched Izod impact strength of atleast 1000 J/m (18 ft-lb/in) at 23° C. with a 10-mil notch in a 6.4 mm(¼-inch) thick bar determined according to ASTM D256.

In another embodiment, certain polyesters useful in the invention canexhibit an increase in notched Izod impact strength when measured at 0°C. of at least 3% or at least 5% or at least 10% or at least 15% ascompared to the notched Izod impact strength when measured at −5° C.with a 10-mil notch in a ⅛-inch thick bar determined according to ASTMD256. In addition, certain other polyesters can also exhibit a retentionof notched Izod impact strength within plus or minus 5% when measured at0° C. through 30° C. with a 10-mil notch in a ⅛-inch thick bardetermined according to ASTM D256.

In yet another embodiment, certain polyesters useful in the inventioncan exhibit a retention in notched Izod impact strength with a loss ofno more than 70% when measured at 23° C. with a 10-mil notch in a ¼-inchthick bar determined according to ASTM D256 as compared to notched Izodimpact strength for the same polyester when measured at the sametemperature with a 10-mil notch in a ⅛-inch thick bar determinedaccording to ASTM D256.

In one embodiment, the polyesters useful in the invention can exhibit aductile-to-brittle transition temperature of less than 0° C. based on a10-mil notch in a ⅛-inch thick bar as defined by ASTM D256.

In one embodiment, the polyesters useful in the invention can exhibit atleast one of the following densities using a gradient density column at23° C.: a density of less than 1.2 g/ml at 23° C.: a density of lessthan 1.2 g/ml at 23° C.; a density of less than 1.18 g/ml at 23° C.; adensity of 0.8 to 1.3 g/ml at 23° C.; a density of 0.80 to 1.2 g/ml at23° C.; a density of 0.80 to less than 1.2 g/ml at 23° C.; a density of1.0 to 1.3 g/ml at 23° C.; a density of 1.0 to 1.2 g/ml at 23° C.; adensity of 1.0 to 1.1 g/ml at 23° C.; a density of 1.13 to 1.3 g/ml at23° C.; a density of 1.13 to 1.2 g/ml at 23° C.

In one embodiment, the polyesters of this invention can be visuallyclear. The term “visually clear” is defined herein as an appreciableabsence of cloudiness, haziness, and/or muddiness, when inspectedvisually. In another embodiment, when the polyesters are blended withpolycarbonate, including, but not limited to, bisphenol Apolycarbonates, the blends can be visually clear.

The present polyesters possess one or more of the following properties.In other embodiments, the polyesters useful in the invention may have ayellowness index (ASTM D-1925) of less than 50 or less than 20.

In one embodiment, the polyesters useful in the invention and/or thepolyester compositions of the invention, with or without toners, canhave color values L*, a* and b* which can be determined using a HunterLab Ultrascan Spectra Colorimeter manufactured by Hunter Associates LabInc., Reston, Va. The color determinations are averages of valuesmeasured on either pellets of the polyesters or plaques or other itemsinjection molded or extruded from them. They are determined by theL*a*b* color system of the CIE (International Commission onIllumination) (translated), wherein L* represents the lightnesscoordinate, a* represents the red/green coordinate, and b* representsthe yellow/blue coordinate. In certain embodiments, the b* values forthe polyesters useful in the invention can be from −10 to less than 10and the L* values can be from 50 to 90. In other embodiments, the b*values for the polyesters useful in the invention can be present in oneof the following ranges: −10 to 9; −10 to 8; −10 to 7; −10 to 6; −10 to5; −10 to 4; −10 to 3; −10 to 2; from −5 to 9; −5 to 8; −5 to 7; −5 to6; −5 to 5; −5 to 4; −5 to 3; −5 to 2; 0 to 9; 0 to 8; 0 to 7; 0 to 6; 0to 5; 0 to 4; 0 to 3; 0 to 2; 1 to 10; 1 to 9; 1 to 8; 1 to 7; 1 to 6; 1to 5; 1 to 4; 1 to 3; and 1 to 2.

In other embodiments, the L* value for the polyesters useful in theinvention can be present in one of the following ranges: 50 to 60; 50 to70; 50 to 80; 50 to 90; 60 to 70; 60 to 80; 60 to 90; 70 to 80; 79 to90.

In some embodiments, use of the polyester compositions useful in theinvention minimizes and/or eliminates the drying step prior to meltprocessing and/or thermoforming.

Although the polyesters useful in this invention can have any moisturecontent, in one embodiment, they may have a moisture content of 0.02 to1.0 weight percent of the total weight of the polyester prior to meltprocessing.

In certain embodiments, the polyesters are dried by conventional methodsfor less than 2 hours at 60° C. to 100° C. prior to melt processing.

The polyesters useful in the invention can be made by processes knownfrom the literature such as, for example, by processes in homogenoussolution, by transesterification processes in the melt, and by two phaseinterfacial processes. Suitable methods include, but are not limited to,the steps of reacting one or more dicarboxylic acids with one or moreglycols at a temperature of 100° C. to 315° C. at a pressure of 0.1 to760 mm Hg for a time sufficient to form a polyester. See U.S. Pat. No.3,772,405 for methods of producing polyesters, the disclosure regardingsuch methods is hereby incorporated herein by reference.

In another aspect, the invention relates to a process for producing apolyester. The process comprises:

-   -   (I) heating a mixture comprising the monomers useful in any of        the polyesters useful in the invention in the presence of a        catalyst at a temperature of 150 to 240° C. for a time        sufficient to produce an initial polyester;    -   (II) heating the initial polyester of step (I) at a temperature        of 240 to 320° C. for 1 to 4 hours; and    -   (III) removing any unreacted glycols.

Suitable catalysts for use in this process include, but are not limitedto, organo-zinc or tin compounds. The use of this type of catalyst iswell known in the art. Examples of catalysts useful in the presentinvention include, but are not limited to, zinc acetate, butyltintris-2-ethylhexanoate, dibutyltin diacetate, and/or dibutyltin oxide.Other catalysts may include, but are not limited to, those based ontitanium, zinc, manganese, lithium, germanium, and cobalt. Catalystamounts can range from 10 ppm to 20,000 ppm or 10 to 10,000 ppm, or 10to 5000 ppm or 10 to 1000 ppm or 10 to 500 ppm, or 10 to 300 ppm or 10to 250 based on the catalyst metal and based on the weight of the finalpolymer. The process can be carried out in either a batch or continuousprocess.

Typically, step (I) can be carried out until 50% by weight or more ofthe 2,2,4,4-tetramethyl-1,3-cyclobutanediol has been reacted. Step (I)may be carried out under pressure, ranging from atmospheric pressure to100 psig. The term “reaction product” as used in connection with any ofthe catalysts useful in the invention refers to any product of apolycondensation or esterification reaction with the catalyst and any ofthe monomers used in making the polyester as well as the product of apolycondensation or esterification reaction between the catalyst and anyother type of additive.

Typically, Step (II) and Step (III) can be conducted at the same time.These steps can be carried out by methods known in the art such as byplacing the reaction mixture under a pressure ranging from 0.002 psig tobelow atmospheric pressure, or by blowing hot nitrogen gas over themixture.

The invention further relates to a polyester product made by the processdescribed above.

The invention further relates to a polymer blend. The blend comprises:

-   -   (a) 5 to 95 weight % of at least one of the polyesters described        above; and    -   (b) 5 to 95 weight % of at least one of the polymeric        components.

Suitable examples of the polymeric components include, but are notlimited to, nylon, other polyesters different from those describedherein, nylon, polyamides such as ZYTEL® from DuPont; polyestersdifferent from those described herein; polystyrene, polystyrenecopolymers, styrene acrylonitrile copolymers, acrylonitrile butadienestyrene copolymers, poly(methylmethacrylate), acrylic copolymers,poly(ether-imides) such as ULTEM® (a poly(ether-imide) from GeneralElectric); polyphenylene oxides such as poly(2,6-dimethylphenyleneoxide) or poly(phenylene oxide)/polystyrene blends such as NORYL 1000®(a blend of poly(2,6-dimethylphenylene oxide) and polystyrene resinsfrom General Electric); other polyesters; polyphenylene sulfides;polyphenylene sulfide/sulfones; poly(ester-carbonates); polycarbonatessuch as LEXAN® (a polycarbonate from General Electric); polysulfones;polysulfone ethers; and poly(ether-ketones) of aromatic dihydroxycompounds or mixtures of any of the other foregoing polymers. The blendscan be prepared by conventional processing techniques known in the art,such as melt blending or solution blending. In one embodiment,polycarbonate is not present in the polyester composition. Ifpolycarbonate is used in a blend in the polyester compositions useful inthe invention, the blends can be visually clear. However, the polyestercompositions useful in the invention also contemplate the exclusion ofpolycarbonate as well as the inclusion of polycarbonate.

Polycarbonates useful in the invention may be prepared according toknown procedures, for example, by reacting the dihydroxyaromaticcompound with a carbonate precursor such as phosgene, a haloformate or acarbonate ester, a molecular weight regulator, an acid acceptor and acatalyst. Methods for preparing polycarbonates are known in the art andare described, for example, in U.S. Pat. No. 4,452,933, where thedisclosure regarding the preparation of polycarbonates is herebyincorporated by reference herein.

Examples of suitable carbonate precursors include, but are not limitedto, carbonyl bromide, carbonyl chloride, or mixtures thereof; diphenylcarbonate; a di(halophenyl)carbonate, e.g.,di(trichlorophenyl)carbonate, di(tribromophenyl)carbonate, and the like;di(alkylphenyl)carbonate, e.g., di(tolyl)carbonate;di(naphthyl)carbonate; di(chloronaphthyl)carbonate, or mixtures thereof;and bis-haloformates of dihydric phenols.

Examples of suitable molecular weight regulators include, but are notlimited to, phenol, cyclohexanol, methanol, alkylated phenols, such asoctylphenol, para-tertiary-butyl-phenol, and the like. In oneembodiment, the molecular weight regulator is phenol or an alkylatedphenol.

The acid acceptor may be either an organic or an inorganic acidacceptor. A suitable organic acid acceptor can be a tertiary amine andincludes, but is not limited to, such materials as pyridine,triethylamine, dimethylaniline, tributylamine, and the like. Theinorganic acid acceptor can be either a hydroxide, a carbonate, abicarbonate, or a phosphate of an alkali or alkaline earth metal.

The catalysts that can be used include, but are not limited to, thosethat typically aid the polymerization of the monomer with phosgene.Suitable catalysts include, but are not limited to, tertiary amines suchas triethylamine, tripropylamine, N,N-dimethylaniline, quaternaryammonium compounds such as, for example, tetraethylammonium bromide,cetyl triethyl ammonium bromide, tetra-n-heptylammonium iodide,tetra-n-propyl ammonium bromide, tetramethyl ammonium chloride,tetra-methyl ammonium hydroxide, tetra-n-butyl ammonium iodide,benzyltrimethyl ammonium chloride and quaternary phosphonium compoundssuch as, for example, n-butyltriphenyl phosphonium bromide andmethyltriphenyl phosphonium bromide.

The polycarbonates useful in the polyester compositions of the inventionalso may be copolyestercarbonates such as those described in U.S. Pat.Nos. 3,169,121; 3,207,814; 4,194,038; 4,156,069; 4,430,484; 4,465,820;and 4,981,898; where the disclosure regarding copolyestercarbonates fromeach of the U.S. patents is incorporated by reference herein.

Copolyestercarbonates useful in this invention can be availablecommercially and/or can be prepared by known methods in the art. Forexample, they can be typically obtained by the reaction of at least onedihydroxyaromatic compound with a mixture of phosgene and at least onedicarboxylic acid chloride, especially isophthaloyl chloride,terephthaloyl chloride, or both.

In addition, the polyester compositions and the polymer blendcompositions containing the polyesters useful in this invention may alsocontain from 0.01 to 25% by weight or 0.01 to 20% by weight or 0.01 to15% by weight or 0.01 to 10% by weight or 0.01 to 5% by weight of thetotal weight of the polyester composition of common additives such ascolorants, dyes, mold release agents, flame retardants, plasticizers,nucleating agents, stabilizers, including but not limited to, UVstabilizers, thermal stabilizers and/or reaction products thereof,fillers, and impact modifiers. Examples of typical commerciallyavailable impact modifiers well known in the art and useful in thisinvention include, but are not limited to, ethylene/propyleneterpolymers; functionalized polyolefins, such as those containing methylacrylate and/or glycidyl methacrylate; styrene-based block copolymericimpact modifiers; and various acrylic core/shell type impact modifiers.For example, UV additives can be incorporated into articles ofmanufacture through addition to the bulk, through application of a hardcoat, or through coextrusion of a cap layer. Residues of such additivesare also contemplated as part of the polyester composition.

The polyesters of the invention can comprise at least one chainextender. Suitable chain extenders include, but are not limited to,multifunctional (including, but not limited to, bifunctional)isocyanates, multifunctional epoxides, including for example, epoxylatednovolacs, and phenoxy resins. In certain embodiments, chain extendersmay be added at the end of the polymerization process or after thepolymerization process. If added after the polymerization process, chainextenders can be incorporated by compounding or by addition duringconversion processes such as injection molding or extrusion. The amountof chain extender used can vary depending on the specific monomercomposition used and the physical properties desired but is generallyabout 0.1 percent by weight to about 10 percent by weight, preferablyabout 0.1 to about 5 percent by weight, based on the total weight of thepolyester.

Thermal stabilizers are compounds that stabilize polyesters duringpolyester manufacture and/or post polymerization including, but notlimited to, phosphorous compounds including but not limited tophosphoric acid, phosphorous acid, phosphonic acid, phosphinic acid,phosphonous acid, and various esters and salts thereof. These can bepresent in the polyester compositions useful in the invention. Theesters can be alkyl, branched alkyl, substituted alkyl, difunctionalalkyl, alkyl ethers, aryl, and substituted aryl. In one embodiment, thenumber of ester groups present in the particular phosphorous compoundcan vary from zero up to the maximum allowable based on the number ofhydroxyl groups present on the thermal stabilizer used. The term“thermal stabilizer” is intended to include the reaction productsthereof. The term “reaction product” as used in connection with thethermal stabilizers of the invention refers to any product of apolycondensation or esterification reaction between the thermalstabilizer and any of the monomers used in making the polyester as wellas the product of a polycondensation or esterification reaction betweenthe catalyst and any other type of additive.

Reinforcing materials may be useful in the compositions of thisinvention. The reinforcing materials may include, but are not limitedto, carbon filaments, silicates, mica, clay, talc, titanium dioxide,Wollastonite, glass flakes, glass beads and fibers, and polymeric fibersand combinations thereof. In one embodiment, the reinforcing materialsare glass, such as, fibrous glass filaments, mixtures of glass and talc,glass and mica, and glass and polymeric fibers.

In another embodiment, the invention further relates to articles ofmanufacture comprising any of the polyesters and blends described above.

The present polyesters and/or polyester blend compositions can be usefulin forming fibers, films, molded articles, containers, and sheeting. Themethods of forming the polyesters into fibers, films, molded articles,containers, and sheeting are well known in the art. Examples ofpotential molded articles include without limitation: medical devicessuch as dialysis equipment, medical packaging, healthcare supplies,commercial foodservice products such as food pans, tumblers and storageboxes, baby bottles, food processors, blender and mixer bowls, utensils,water bottles, crisper trays, washing machine fronts, and vacuum cleanerparts. Other potential molded articles could include, but are notlimited to, ophthalmic lenses and frames. For instance, this material isenvisioned to make bottles, including, but not limited to, baby bottles,as it is visually clear, tough, heat resistant, and displays goodhydrolytic stability.

The invention further relates to articles of manufacture. These articlesinclude, but are not limited to, injection blow molded articles,injection stretch blow molded articles, extrusion blow molded articles,extrusion stretch blow molded articles, calendered articles, compressionmolded articles, and solution casted articles. Methods of making thearticles of manufacture, include, but are not limited to, extrusion blowmolding, extrusion stretch blow molding, injection blow molding,injection stretch blow molding, calendering, compression molding, andsolution casting.

In another embodiment, the invention further relates to articles ofmanufacture comprising the film(s) and/or sheet(s) containing polyestercompositions described herein.

The films and/or sheets useful in the present invention can be of anythickness which would be apparent to one of ordinary skill in the art.In one embodiment, the film(s) of the invention have a thickness of nomore than 40 mils. In one embodiment, the film(s) of the invention havea thickness of no more than 35 mils. In one embodiment, the film(s) ofthe invention have a thickness of no more than 30 mils. In oneembodiment, the film(s) of the invention have a thickness of no morethan 25 mils. In one embodiment, the film(s) of the invention have athickness of no more than 20 mils.

In one embodiment, the sheet(s) of the invention have a thickness of noless than 20 mils. In another embodiment, the sheet(s) of the inventionhave a thickness of no less than 25 mils. In another embodiment, thesheet(s) of the invention have a thickness of no less than 30 mils. Inanother embodiment, the sheet(s) of the invention have a thickness of noless than 35 mils. In another embodiment, the sheet(s) of the inventionhave a thickness of no less than 40 mils.

The invention further relates to the film(s) and/or sheet(s) comprisingthe polyester compositions of the invention. The methods of forming thepolyesters into film(s) and/or sheet(s) are well known in the art.Examples of film(s) and/or sheet(s) of the invention including but notlimited to extruded film(s) and/or sheet(s), calendered film(s) and/orsheet(s), compression molded film(s) and/or sheet(s), solution castedfilm(s) and/or sheet(s). Methods of making film and/or sheet include butare not limited to extrusion, calendering, compression molding, andsolution casting.

Examples of potential articles made from film and/or sheet include, butare not limited, to uniaxially stretched film, biaxially stretched film,shrink film (whether or not uniaxially or biaxially stretched), liquidcrystal display film (including, but not limited to, diffuser sheets,compensation films and protective films), thermoformed sheet, graphicarts film, outdoor signs, skylights, coating(s), coated articles,painted articles, laminates, laminated articles, and/or multiwall filmsor sheets.

Examples of graphic arts film include, but are not limited to,nameplates, membrane switch overlays; point-of-purchase displays; flator in-mold decorative panels on washing machines; flat touch panels onrefrigerators; flat panel on ovens; decorative interior trim forautomobiles; instrument clusters for automobiles; cell phone covers;heating and ventilation control displays; automotive console panels;automotive gear shift panels; control displays or warning signals forautomotive instrument panels; facings, dials or displays on householdappliances; facings, dials or displays on washing machines; facings,dials or displays on dishwashers; keypads for electronic devices;keypads for mobile phones, PDAs (hand-held computers) or remotecontrols; displays for electronic devices; displays for hand-heldelectronic devices such as phones and PDAs; panels and housings formobile or standard phones; logos on electronic devices; and logos forhand-held phones.

Multiwall film or sheet refers to sheet extruded as a profile consistingof multiple layers that are connected to each other by means of verticalribs. Examples of multiwall film or sheet include but are not limited togreenhouses and commercial canopies.

Examples of extruded articles comprising the polyesters useful in thisinvention include, but are not limited to, film for graphic artsapplications, outdoor signs, skylights, multiwall film, plastic film forplastic glass laminates, and liquid crystal display (LCD) films,including but not limited to, diffuser sheets, compensation films, andprotective films for LCDs.

As used herein, the abbreviation “wt” means “weight”.

The following examples further illustrate how the compositions of matterof the invention can be made and evaluated, and are intended to bepurely exemplary of the invention and are not intended to limit thescope thereof. Unless indicated otherwise, parts are parts by weight,temperature is in degrees C. or is at room temperature, and pressure isat or near atmospheric.

EXAMPLES

The inherent viscosity of the polyesters was determined in 60/40 (wt/wt)phenol/tetrachloroethane at a concentration of 0.5 g/100 ml at 25° C.

Unless stated otherwise, the glass transition temperature (T_(g)) wasdetermined using a TA DSC 2920 instrument from Thermal AnalystInstruments at a scan rate of 20° C./min according to ASTM D3418.

The glycol content and the cis/trans ratio of the compositions weredetermined by proton nuclear magnetic resonance (NMR) spectroscopy. AllNMR spectra were recorded on a JEOL Eclipse Plus 600 MHz nuclearmagnetic resonance spectrometer using either chloroform-trifluoroaceticacid (70-30 volume/volume) for polymers or, for oligomeric samples,60/40(wt/wt) phenol/tetrachloroethane with deuterated chloroform addedfor lock. Peak assignments for 2,2,4,4-tetramethyl-1,3-cyclobutanediolresonances were made by comparison to model mono- and dibenzoate estersof 2,2,4,4-tetramethyl-1,3-cyclobutanediol. These model compoundsclosely approximate the resonance positions found in the polymers andoligomers.

The crystallization half-time, t½, was determined by measuring the lighttransmission of a sample via a laser and photo detector as a function oftime on a temperature controlled hot stage. This measurement was done byexposing the polymers to a temperature, T_(max), and then cooling it tothe desired temperature. The sample was then held at the desiredtemperature by a hot stage while transmission measurements were made asa function of time. Initially, the sample was visually clear with highlight transmission and became opaque as the sample crystallized. Thecrystallization half-time was recorded as the time at which the lighttransmission was halfway between the initial transmission and the finaltransmission. T_(max) is defined as the temperature required to melt thecrystalline domains of the sample (if crystalline domains are present).The T_(max) reported in the examples below represents the temperature atwhich each sample was heated to condition the sample prior tocrystallization half time measurement. The T_(max) temperature isdependant on composition and is typically different for each polyester.For example, PCT may need to be heated to some temperature greater than290° C. to melt the crystalline domains.

Density was determined using a gradient density column at 23° C.

The melt viscosity reported herein was measured by using a RheometricsDynamic Analyzer (RDA II). The melt viscosity was measured as a functionof shear rate, at frequencies ranging from 1 to 400 rad/sec, at thetemperatures reported. The zero shear melt viscosity (η_(o)) is the meltviscosity at zero shear rate estimated by extrapolating the data byknown models in the art. This step is automatically performed by theRheometrics Dynamic Analyzer (RDA II) software.

The polymers were dried at a temperature ranging from 80 to 100° C. in avacuum oven for 24 hours and injection molded on a Boy 22S moldingmachine to give ⅛×½×5-inch and ¼×½×5-inch flexure bars. These bars werecut to a length of 2.5 inch and notched down the ½ inch width with a10-mil notch in accordance with ASTM D256. The average Izod impactstrength at 23° C. was determined from measurements on 5 specimens.

In addition, 5 specimens were tested at various temperatures using 5° C.increments in order to determine the brittle-to-ductile transitiontemperature. The brittle-to-ductile transition temperature is defined asthe temperature at which 50% of the specimens fail in a brittle manneras denoted by ASTM D256.

Color values reported herein were determined using a Hunter LabUltrascan Spectra Colorimeter manufactured by Hunter Associates LabInc., Reston, Va. The color determinations were averages of valuesmeasured on either pellets of the polyesters or plaques or other itemsinjection molded or extruded from them. They were determined by theL*a*b* color system of the CIE (International Commission onIllumination) (translated), wherein L* represents the lightnesscoordinate, a* represents the red/green coordinate, and b* representsthe yellow/blue coordinate.

In addition, 10-mil films were compression molded using a Carver pressat 240° C.

Unless otherwise specified, the cis/trans ratio of the 1,4cyclohexanedimethanol used in the following examples was approximately30/70, and could range from 35/65 to 25/75. Unless otherwise specified,the cis/trans ratio of the 2,2,4,4-tetramethyl-1,3-cyclobutanediol usedin the following examples was approximately 50/50.

The following abbreviations apply throughout the working examples andfigures:

TPA Terephthalic acid DMT Dimethyl therephthalate TMCD2,2,4,4-tetramethyl-1,3-cyclobutanediol CHDM 1,4-cyclohexanedimethanolIV Inherent viscosity η₀ Zero shear melt viscosity T_(g) Glasstransition temperature T_(bd) Brittle-to-ductile transition temperatureT_(max) Conditioning temperature for crystallization half timemeasurements

Example 1

This example illustrates that 2,2,4,4-tetramethyl-1,3-cyclobutanediol ismore effective at reducing the crystallization rate of PCT than ethyleneglycol or isophthalic acid. In addition, this example illustrates thebenefits of 2,2,4,4-tetramethyl-1,3-cyclobutanediol on the glasstransition temperature and density.

A variety of copolyesters were prepared as described below. Thesecopolyesters were all made with 200 ppm dibutyl tin oxide as thecatalyst in order to minimize the effect of catalyst type andconcentration on nucleation during crystallization studies. Thecis/trans ratio of the 1,4-cyclohexanedimethanol was 31/69 while thecis/trans ratio of the 2,2,4,4-tetramethyl-1,3-cyclobutanediol isreported in Table 1.

For purposes of this example, the samples had sufficiently similarinherent viscosities thereby effectively eliminating this as a variablein the crystallization rate measurements.

Crystallization half-time measurements from the melt were made attemperatures from 140 to 200° C. at 10° C. increments and are reportedin Table 1. The fastest crystallization half-time for each sample wastaken as the minimum value of crystallization half-time as a function oftemperature, typically occurring around 170 to 180° C. The fastestcrystallization half-times for the samples are plotted in FIG. 1 as afunction of mole % comonomer modification to PCT.

The data shows that 2,2,4,4-tetramethyl-1,3-cyclobutanediol is moreeffective than ethylene glycol and isophthalic acid at decreasing thecrystallization rate (i.e., increasing the crystallization half-time).In addition, 2,2,4,4-tetramethyl-1,3-cyclobutanediol increases T_(g) andlowers density.

TABLE 1 Crystallization Half-times (min) at at at at at at at ComonomerIV Density T_(g) T_(max) 140° C. 150° C. 160° C. 170° C. 180° C. 190° C.200° C. Example (mol %)¹ (dl/g) (g/ml) (° C.) (° C.) (min) (min) (min)(min) (min) (min) (min) 1A 20.2% A² 0.630 1.198 87.5 290 2.7 2.1 1.3 1.20.9 1.1 1.5 1B 19.8% B 0.713 1.219 87.7 290 2.3 2.5 1.7 1.4 1.3 1.4 1.71C 20.0% C 0.731 1.188 100.5 290 >180 >60 35.0 23.3 21.7 23.3 25.2 1D40.2% A² 0.674 1.198 81.2 260 18.7 20.0 21.3 25.0 34.0 59.9 96.1 1E34.5% B 0.644 1.234 82.1 260 8.5 8.2 7.3 7.3 8.3 10.0 11.4 1F 40.1% C0.653 1.172 122.0 260 >10 days >5 days >5 days 19204 >5 days >5 days >5days 1G 14.3% D 0.646³ 1.188 103.0 290 55.0 28.8 11.6 6.8 4.8 5.0 5.5 1H15.0% E 0.728⁴ 1.189 99.0 290 25.4 17.1 8.1 5.9 4.3 2.7 5.1 ¹The balanceof the diol component of the polyesters in Table 1 is1,4-cyclohexanedimethanol; and the balance of the dicarboxylic acidcomponent of the polyesters in Table 1 is dimethyl terephthalate; if thedicarboxylic acid is not described, it is 100 mole % dimethylterephthalate. ²100 mole % 1,4-cyclohexanedimethanol. ³A film waspressed from the ground polyester of Example 1G at 240° C. The resultingfilm had an inherent viscosity value of 0.575 dL/g. ⁴A film was pressedfrom the ground polyester of Example 1H at 240° C. The resulting filmhad an inherent viscosity value of 0.0.652 dL/g. where: A is IsophthalicAcid B is Ethylene Glycol C is 2,2,4,4-Tetramethyl-1,3-cyclobutanediol(approx. 50/50 cis/trans) D is 2,2,4,4-Tetramethyl-1,3-cyclobutanediol(98/2 cis/trans) E is 2,2,4,4-Tetramethyl-1,3-cyclobutanediol (5/95cis/trans)

As shown in Table 1 and FIG. 1, 2,2,4,4-tetramethyl-1,3-cyclobutanediolis more effective than other comonomers, such ethylene glycol andisophthalic acid, at increasing the crystallization half-time, i.e., thetime required for a polymer to reach half of its maximum crystallinity.By decreasing the crystallization rate of PCT (increasing thecrystallization half-time), amorphous articles based on2,2,4,4-tetramethyl-1,3-cyclobutanediol-modified PCT as described hereinmay be fabricated by methods known in the art. As shown in Table 1,these materials can exhibit higher glass transition temperatures andlower densities than other modified PCT copolyesters.

Preparation of the polyesters shown on Table 1 is described below.

Example 1A

This example illustrates the preparation of a copolyester with a targetcomposition of 80 mol % dimethyl terephthalate residues, 20 mol %dimethyl isophthalate residues, and 100 mol % 1,4-cyclohexanedimethanolresidues (28/72 cis/trans).

A mixture of 56.63 g of dimethyl terephthalate, 55.2 g of1,4-cyclohexanedimethanol, 14.16 g of dimethyl isophthalate, and 0.0419g of dibutyl tin oxide was placed in a 500-milliliter flask equippedwith an inlet for nitrogen, a metal stirrer, and a short distillationcolumn. The flask was placed in a Wood's metal bath already heated to210° C. The stirring speed was set to 200 RPM throughout the experiment.The contents of the flask were heated at 210° C. for 5 minutes and thenthe temperature was gradually increased to 290° C. over 30 minutes. Thereaction mixture was held at 290° C. for 60 minutes and then vacuum wasgradually applied over the next 5 minutes until the pressure inside theflask reached 100 mm of Hg. The pressure inside the flask was furtherreduced to 0.3 mm of Hg over the next 5 minutes. A pressure of 0.3 mm ofHg was maintained for a total time of 90 minutes to remove excessunreacted diols. A high melt viscosity, visually clear and colorlesspolymer was obtained with a glass transition temperature of 87.5° C. andan inherent viscosity of 0.63 dl/g. NMR analysis showed that the polymerwas composed of 100 mol % 1,4-cyclohexanedimethanol residues and 20.2mol % dimethyl isophthalate residues.

Example 1B

This example illustrates the preparation of a copolyester with a targetcomposition of 100 mol % dimethyl terephthalate residues, 20 mol %ethylene glycol residues, and 80 mol % 1,4-cyclohexanedimethanolresidues (32/68 cis/trans).

A mixture of 77.68 g of dimethyl terephthalate, 50.77 g of1,4-cyclohexanedimethanol, 27.81 g of ethylene glycol, and 0.0433 g ofdibutyl tin oxide was placed in a 500-milliliter flask equipped with aninlet for nitrogen, a metal stirrer, and a short distillation column.The flask was placed in a Wood's metal bath already heated to 200° C.The stirring speed was set to 200 RPM throughout the experiment. Thecontents of the flask were heated at 200° C. for 60 minutes and then thetemperature was gradually increased to 210° C. over 5 minutes. Thereaction mixture was held at 210° C. for 120 minutes and then heated upto 280° C. in 30 minutes. Once at 280° C., vacuum was gradually appliedover the next 5 minutes until the pressure inside the flask reached 100mm of Hg. The pressure inside the flask was further reduced to 0.3 mm ofHg over the next 10 minutes. A pressure of 0.3 mm of Hg was maintainedfor a total time of 90 minutes to remove excess unreacted diols. A highmelt viscosity, visually clear and colorless polymer was obtained with aglass transition temperature of 87.7° C. and an inherent viscosity of0.71 dl/g. NMR analysis showed that the polymer was composed of 19.8 mol% ethylene glycol residues.

Example 1C

This example illustrates the preparation of a copolyester with a targetcomposition of 100 mol % dimethyl terephthalate residues, 20 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues, and 80 mol %1,4-cyclohexanedimethanol residues (31/69 cis/trans).

A mixture of 77.68 g of dimethyl terephthalate, 48.46 g of1,4-cyclohexanedimethanol, 17.86 g of2,2,4,4-tetramethyl-1,3-cyclobutanediol, and 0.046 g of dibutyl tinoxide was placed in a 500-milliliter flask equipped with an inlet fornitrogen, a metal stirrer, and a short distillation column. Thispolyester was prepared in a manner similar to that described in Example1A. A high melt viscosity, visually clear and colorless polymer wasobtained with a glass transition temperature of 100.5° C. and aninherent viscosity of 0.73 dl/g. NMR analysis showed that the polymerwas composed of 80.5 mol % 1,4-cyclohexanedimethanol residues and 19.5mol % 2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Example 1D

This example illustrates the preparation of a copolyester with a targetcomposition of 100 mol % dimethyl terephthalate residues, 40 mol %dimethyl isophthalate residues, and 100 mol % 1,4-cyclohexanedimethanolresidues (28/72 cis/trans).

A mixture of 42.83 g of dimethyl terephthalate, 55.26 g of1,4-cyclohexanedimethanol, 28.45 g of dimethyl isophthalate, and 0.0419g of dibutyl tin oxide was placed in a 500-milliliter flask equippedwith an inlet for nitrogen, a metal stirrer, and a short distillationcolumn. The flask was placed in a Wood's metal bath already heated to210° C. The stirring speed was set to 200 RPM throughout the experiment.The contents of the flask were heated at 210° C. for 5 minutes and thenthe temperature was gradually increased to 290° C. over 30 minutes. Thereaction mixture was held at 290° C. for 60 minutes and then vacuum wasgradually applied over the next 5 minutes until the pressure inside theflask reached 100 mm of Hg. The pressure inside the flask was furtherreduced to 0.3 mm of Hg over the next 5 minutes. A pressure of 0.3 mm ofHg was maintained for a total time of 90 minutes to remove excessunreacted diols. A high melt viscosity, visually clear and colorlesspolymer was obtained with a glass transition temperature of 81.2° C. andan inherent viscosity of 0.67 dl/g. NMR analysis showed that the polymerwas composed of 100 mol % 1,4-cyclohexanedimethanol residues and 40.2mol % dimethyl isophthalate residues.

Example 1E

This example illustrates the preparation of a copolyester with a targetcomposition of 100 mol % dimethyl terephthalate residues, 40 mol %ethylene glycol residues, and 60 mol % 1,4-cyclohexanedimethanolresidues (31/69 cis/trans).

A mixture of 81.3 g of dimethyl terephthalate, 42.85 g of1,4-cyclohexanedimethanol, 34.44 g of ethylene glycol, and 0.0419 g ofdibutyl tin oxide was placed in a 500-milliliter flask equipped with aninlet for nitrogen, a metal stirrer, and a short distillation column.The flask was placed in a Wood's metal bath already heated to 200° C.The stirring speed was set to 200 RPM throughout the experiment. Thecontents of the flask were heated at 200° C. for 60 minutes and then thetemperature was gradually increased to 210° C. over 5 minutes. Thereaction mixture was held at 210° C. for 120 minutes and then heated upto 280° C. in 30 minutes. Once at 280° C., vacuum was gradually appliedover the next 5 minutes until the pressure inside the flask reached 100mm of Hg. The pressure inside the flask was further reduced to 0.3 mm ofHg over the next 10 minutes. A pressure of 0.3 mm of Hg was maintainedfor a total time of 90 minutes to remove excess unreacted diols. A highmelt viscosity, visually clear and colorless polymer was obtained with aglass transition temperature of 82.1° C. and an inherent viscosity of0.64 dl/g. NMR analysis showed that the polymer was composed of 34.5 mol% ethylene glycol residues.

Example 1F

This example illustrates the preparation of a copolyester with a targetcomposition of 100 mol % dimethyl terephthalate residues, 40 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues, and 60 mol %1,4-cyclohexanedimethanol residues (31/69 cis/trans).

A mixture of 77.4 g of dimethyl terephthalate, 36.9 g of1,4-cyclohexanedimethanol, 32.5 g of2,2,4,4-tetramethyl-1,3-cyclobutanediol, and 0.046 g of dibutyl tinoxide was placed in a 500-milliliter flask equipped with an inlet fornitrogen, a metal stirrer, and a short distillation column. The flaskwas placed in a Wood's metal bath already heated to 210° C. The stirringspeed was set to 200 RPM throughout the experiment. The contents of theflask were heated at 210° C. for 3 minutes and then the temperature wasgradually increased to 260° C. over 30 minutes. The reaction mixture washeld at 260° C. for 120 minutes and then heated up to 290° C. in 30minutes. Once at 290° C., vacuum was gradually applied over the next 5minutes until the pressure inside the flask reached 100 mm of Hg. Thepressure inside the flask was further reduced to 0.3 mm of Hg over thenext 5 minutes. A pressure of 0.3 mm of Hg was maintained for a totaltime of 90 minutes to remove excess unreacted diols. A high meltviscosity, visually clear and colorless polymer was obtained with aglass transition temperature of 122° C. and an inherent viscosity of0.65 dl/g. NMR analysis showed that the polymer was composed of 59.9 mol% 1,4-cyclohexanedimethanol residues and 40.1 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Example 1G

This example illustrates the preparation of a copolyester with a targetcomposition of 100 mol % dimethyl terephthalate residues, 20 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues (98/2 cis/trans), and80 mol % 1,4-cyclohexanedimethanol residues (31/69 cis/trans).

A mixture of 77.68 g of dimethyl terephthalate, 48.46 g of1,4-cyclohexanedimethanol, 20.77 g of2,2,4,4-tetramethyl-1,3-cyclobutanediol, and 0.046 g of dibutyl tinoxide was placed in a 500-milliliter flask equipped with an inlet fornitrogen, a metal stirrer, and a short distillation column. The flaskwas placed in a Wood's metal bath already heated to 210° C. The stirringspeed was set to 200 RPM throughout the experiment. The contents of theflask were heated at 210° C. for 3 minutes and then the temperature wasgradually increased to 260° C. over 30 minutes. The reaction mixture washeld at 260° C. for 120 minutes and then heated up to 290° C. in 30minutes. Once at 290° C., vacuum was gradually applied over the next 5minutes until the pressure inside the flask reached 100 mm of Hg and thestirring speed was also reduced to 100 RPM. The pressure inside theflask was further reduced to 0.3 mm of Hg over the next 5 minutes andthe stirring speed was reduced to 50 RPM. A pressure of 0.3 mm of Hg wasmaintained for a total time of 60 minutes to remove excess unreacteddiols. A high melt viscosity, visually clear and colorless polymer wasobtained with a glass transition temperature of 103° C. and an inherentviscosity of 0.65 dl/g. NMR analysis showed that the polymer wascomposed of 85.7 mol % 1,4-cyclohexanedimethanol residues and 14.3 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Example 1H

This example illustrates the preparation of a copolyester with a targetcomposition of 100 mol % dimethyl terephthalate residues, 20 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues (5/95 cis/trans), and80 mol % 1,4-cyclohexanedimethanol residues (31/69 cis/trans).

A mixture of 77.68 g of dimethyl terephthalate, 48.46 g of1,4-cyclohexanedimethanol, 20.77 g of2,2,4,4-tetramethyl-1,3-cyclobutanediol, and 0.046 g of dibutyl tinoxide was placed in a 500-milliliter flask equipped with an inlet fornitrogen, a metal stirrer, and a short distillation column. The flaskwas placed in a Wood's metal bath already heated to 210° C. The stirringspeed was set to 200 RPM at the beginning of the experiment. Thecontents of the flask were heated at 210° C. for 3 minutes and then thetemperature was gradually increased to 260° C. over 30 minutes. Thereaction mixture was held at 260° C. for 120 minutes and then heated upto 290° C. in 30 minutes. Once at 290° C., vacuum was gradually appliedover the next 5 minutes with a set point of 100 mm of Hg and thestirring speed was also reduced to 100 RPM. The pressure inside theflask was further reduced to a set point of 0.3 mm of Hg over the next 5minutes and the stirring speed was reduced to 50 RPM. This pressure wasmaintained for a total time of 60 minutes to remove excess unreacteddiols. It was noted that the vacuum system failed to reach the set pointmentioned above, but produced enough vacuum to produce a high meltviscosity, visually clear and colorless polymer with a glass transitiontemperature of 99° C. and an inherent viscosity of 0.73 dl/g. NMRanalysis showed that the polymer was composed of 85 mol %1,4-cyclohexanedimethanol residues and 15 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Example 2

This example illustrates that 2,2,4,4-tetramethyl-1,3-cyclobutanediolimproves the toughness of PCT-based copolyesters (polyesters containingterephthalic acid and 1,4-cyclohexanedimethanol).

Copolyesters based on 2,2,4,4-tetramethyl-1,3-cyclobutanediol wereprepared as described below. The cis/trans ratio of the1,4-cyclohexanedimethanol was approximately 31/69 for all samples.Copolyesters based on ethylene glycol and 1,4-cyclohexanedimethanol werecommercial polyesters. The copolyester of Example 2A (Eastar PCTG 5445)was obtained from Eastman Chemical Co. The copolyester of Example 2B wasobtained from Eastman Chemical Co. under the trade name Spectar. Example2C and Example 2D were prepared on a pilot plant scale (each a 15-lbbatch) following an adaptation of the procedure described in Example 1Aand having the inherent viscosities and glass transition temperaturesdescribed in Table 2 below. Example 2C was prepared with a target tinamount of 300 ppm (Dibutyltin Oxide). The final product contained 295ppm tin. The color values for the polyester of Example 2C were L*=77.11;a*=−1.50; and b*=5.79. Example 2D was prepared with a target tin amountof 300 ppm (Dibutyltin Oxide). The final product contained 307 ppm tin.The color values for the polyester of Example 2D were L*=66.72;a*=−1.22; and b*=16.28.

Materials were injection molded into bars and subsequently notched forIzod testing. The notched Izod impact strengths were obtained as afunction of temperature and are also reported in Table 2.

For a given sample, the Izod impact strength undergoes a majortransition in a short temperature span. For instance, the Izod impactstrength of a copolyester based on 38 mol % ethylene glycol undergoesthis transition between 15 and 20° C. This transition temperature isassociated with a change in failure mode; brittle/low energy failures atlower temperatures and ductile/high energy failures at highertemperatures. The transition temperature is denoted as thebrittle-to-ductile transition temperature, T_(bd), and is a measure oftoughness. T_(bd) is reported in Table 2 and plotted against mol %comonomer in FIG. 2.

The data shows that adding 2,2,4,4-tetramethyl-1,3-cyclobutanediol toPCT lowers T_(bd) and improves the toughness, as compared to ethyleneglycol, which increases T_(bd) of PCT.

TABLE 2 Notched Izod Impact Energy (ft-lb/in) Ex- Comonomer IV T_(g)T_(bd) at at at at at at at at at ample (mol %)¹ (dl/g) (° C.) (° C.)−20° C. −15° C. −10° C. −5° C. at 0° C. at 5° C. 10° C. 15° C. 20° C.25° C. 30° C. 2A 38.0% B 0.68 86 18 NA NA NA 1.5 NA NA 1.5 1.5 32 32 NA2B 69.0% B 0.69 82 26 NA NA NA NA NA NA 2.1 NA 2.4 13.7 28.7 2C 22.0% C0.66 106 −5 1.5 NA 12 23 23 NA 23 NA NA NA NA 2D 42.8% C 0.60 133 −122.5 2.5 11 NA 14 NA NA NA NA NA NA ¹The balance of the glycol componentof the polyesters in the Table is 1,4-cyclohexanedimethanol. Allpolymers were prepared from 100 mole % dimethyl terephthalate. NA = Notavailable. where: B is Ethylene glycol C is2,2,4,4-Tetramethyl-1,3-cyclobutanediol (50/50 cis/trans)

Example 3

This example illustrates that 2,2,4,4-tetramethyl-1,3-cyclobutanediolcan improve the toughness of PCT-based copolyesters (polyesterscontaining terephthalic acid and 1,4-cyclohexanedimethanol). Polyestersprepared in this example comprise from 15 to 25 mol % of2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Copolyesters based on dimethyl terephthalate,2,2,4,4-tetramethyl-1,3-cyclobutanediol, and 1,4-cyclohexanedimethanolwere prepared as described below, having the composition and propertiesshown on Table 3. The balance up to 100 mol % of the diol component ofthe polyesters in Table 3 was 1,4-cyclohexanedimethanol (31/69cis/trans).

Materials were injection molded into both 3.2 mm and 6.4 mm thick barsand subsequently notched for Izod impact testing. The notched Izodimpact strengths were obtained at 23° C. and are reported in Table 3.Density, Tg, and crystallization halftime were measured on the moldedbars. Melt viscosity was measured on pellets at 290° C.

TABLE 3 Compilation of various properties for certain polyesters usefulin the invention Notched Notched Izod of Izod of 3.2 mm 6.4 mm Meltthick thick Crystallization Viscosity Pellet Molded bars at bars atSpecific Halftime from at 1 rad/sec TMCD % cis IV Bar IV 23° C. 23° C.Gravity Tg melt at 170° C. at 290° C. Example mole % TMCD (dl/g) (dl/g)(J/m) (J/m) (g/mL) (° C.) (min) (Poise) A 15 48.8 0.736 0.707 1069 8781.184 104 15 5649 B 18 NA 0.728 0.715 980 1039 1.183 108 22 6621 C 20 NA0.706 0.696 1006 1130 1.182 106 52 6321 D 22 NA 0.732 0.703 959 9881.178 108 63 7161 E 21 NA 0.715 0.692 932 482 1.179 110 56 6162 F 24 NA0.708 0.677 976 812 1.180 109 58 6282 G 23 NA 0.650 0.610 647 270 1.182107 46 3172 H 23 47.9 0.590 0.549 769 274 1.181 106 47 1736 I 23 48.10.531 0.516 696 352 1.182 105 19 1292 J 23 47.8 0.364 NA NA NA NA 98 NA167 NA = Not available.

Example 3A

21.24 lb (49.71 gram-mol) dimethyl terephthalate, 14.34 lb (45.21gram-mol) 1,4-cyclohexanedimethanol, and 4.58 lb (14.44 gram-mol)2,2,4,4-tetramethyl-1,3-cyclobutanediol were reacted together in thepresence of 200 ppm of the catalyst butyltin tris(2-ethylhexanoate). Thereaction was carried out under a nitrogen gas purge in an 18-gallonstainless steel pressure vessel fitted with a condensing column, avacuum system, and a HELICONE-type agitator. With the agitator runningat 25 RPM, the reaction mixture temperature was increased to 250° C. andthe pressure was increased to 20 psig. The reaction mixture was held for2 hours at 250° C. and at a pressure of 20 psig. The pressure was thendecreased to 0 psig at a rate of 3 psig/minute. The temperature of thereaction mixture was then increased to 270° C. and the pressure wasdecreased to 90 mm of Hg. After a 1 hour hold time at 270° C. and 90 mmof Hg, the agitator speed was decreased to 15 RPM, the reaction mixturetemperature was increased to 290° C., and the pressure was decreased to<1 mm of Hg. The reaction mixture was held at 290° C. and at a pressureof <1 mm of Hg until the power draw to the agitator no longer increased(70 minutes). The pressure of the pressure vessel was then increased to1 atmosphere using nitrogen gas. The molten polymer was then extrudedfrom the pressure vessel. The cooled, extruded polymer was ground topass a 6-mm screen. The polymer had an inherent viscosity of 0.736 dL/gand a Tg of 104° C. NMR analysis showed that the polymer was composed of85.4 mol % 1,4-cyclohexane-dimethanol residues and 14.6 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues. The polymer had colorvalues of: L*=78.20, a*=−1.62, and b*=6.23.

Example 3B to Example 3D

The polyesters described in Example 3B to Example 3D were preparedfollowing a procedure similar to the one described for Example 3A. Thecomposition and properties of these polyesters are shown in Table 3.

Example 3E

21.24 lb (49.71 gram-mol) dimethyl terephthalate, 12.61 lb (39.77gram-mol) 1,4-cyclohexanedimethanol, and 6.30 lb (19.88 gram-mol)2,2,4,4-tetramethyl-1,3-cyclobutanediol were reacted together in thepresence of 200 ppm of the catalyst butyltin tris(2-ethylhexanoate). Thereaction was carried out under a nitrogen gas purge in an 18-gallonstainless steel pressure vessel fitted with a condensing column, avacuum system, and a HELICONE-type agitator. With the agitator runningat 25 RPM, the reaction mixture temperature was increased to 250° C. andthe pressure was increased to 20 psig. The reaction mixture was held for2 hours at 250° C. and 20 psig pressure. The pressure was then decreasedto 0 psig at a rate of 3 psig/minute. The temperature of the reactionmixture was then increased to 270° C. and the pressure was decreased to90 mm of Hg. After a 1 hour hold time at 270° C. and 90 mm of Hg, theagitator speed was decreased to 15 RPM, the reaction mixture temperaturewas increased to 290° C., and the pressure was decreased to <1 mm of Hg.The reaction mixture was held at 290° C. and at a pressure of <1 mm ofHg for 60 minutes. The pressure of the pressure vessel was thenincreased to 1 atmosphere using nitrogen gas. The molten polymer wasthen extruded from the pressure vessel. The cooled, extruded polymer wasground to pass a 6-mm screen. The polymer had an inherent viscosity of0.715 dL/g and a Tg of 110° C. X-ray analysis showed that the polyesterhad 223 ppm tin. NMR analysis showed that the polymer was composed of78.6 mol % 1,4-cyclohexane-dimethanol residues and 21.4 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues. The polymer had colorvalues of: L*=76.45, a*=−1.65, and b*=6.47.

Example 3F

The polyester described in Example 3F was prepared following a proceduresimilar to the one described for Example 3A. The composition andproperties of this polyester are shown in Table 3.

Example 3G

The polyester described in Example 3G was prepared following a proceduresimilar to the one described for Example 3A. The composition andproperties of this polyester are shown in Table 3.

Example 3H

21.24 lb (49.71 gram-mol) dimethyl terephthalate, 12.61 lb (39.77gram-mol) 1,4-cyclohexanedimethanol, and 6.30 lb (19.88 gram-mol)2,2,4,4-tetramethyl-1,3-cyclobutanediol were reacted together in thepresence of 200 ppm of the catalyst butyltin tris(2-ethylhexanoate). Thereaction was carried out under a nitrogen gas purge in an 18-gallonstainless steel pressure vessel fitted with a condensing column, avacuum system, and a HELICONE-type agitator. With the agitator runningat 25 RPM, the reaction mixture temperature was increased to 250° C. andthe pressure was increased to 20 psig. The reaction mixture was held for2 hours at 250° C. and 20 psig pressure. The pressure was then decreasedto 0 psig at a rate of 3 psig/minute. The temperature of the reactionmixture was then increased to 270° C. and the pressure was decreased to90 mm of Hg. After a 1 hour hold time at 270° C. and 90 mm of Hg, theagitator speed was decreased to 15 RPM, the reaction mixture temperaturewas increased to 290° C., and the pressure was decreased to <1 mm of Hg.The reaction mixture was held at 290° C. and at a pressure of <1 mm ofHg for 12 minutes. The pressure of the pressure vessel was thenincreased to 1 atmosphere using nitrogen gas. The molten polymer wasthen extruded from the pressure vessel. The cooled, extruded polymer wasground to pass a 6-mm screen. The polymer had an inherent viscosity of0.590 dL/g and a Tg of 106° C. NMR analysis showed that the polymer wascomposed of 77.1 mol % 1,4-cyclohexane-dimethanol residues and 22.9 mol% 2,2,4,4-tetramethyl-1,3-cyclobutanediol residues. The polymer hadcolor values of: L*=83.27, a*=−1.34, and b*=5.08.

Example 3I

21.24 lb (49.71 gram-mol) dimethyl terephthalate, 12.61 lb (39.77gram-mol) 1,4-cyclohexanedimethanol, and 6.30 lb (19.88 gram-mol)2,2,4,4-tetramethyl-1,3-cyclobutanediol were reacted together in thepresence of 200 ppm of the catalyst butyltin tris(2-ethylhexanoate). Thereaction was carried out under a nitrogen gas purge in an 18-gallonstainless steel pressure vessel fitted with a condensing column, avacuum system, and a HELICONE-type agitator. With the agitator runningat 25 RPM, the reaction mixture temperature was increased to 250° C. andthe pressure was increased to 20 psig. The reaction mixture was held for2 hours at 250° C. and 20 psig pressure. The pressure was then decreasedto 0 psig at a rate of 3 psig/minute. The temperature of the reactionmixture was then increased to 270° C. and the pressure was decreased to90 mm of Hg. After a 1 hour hold time at 270° C. and 90 mm of Hg, theagitator speed was decreased to 15 RPM, the reaction mixture temperaturewas increased to 290° C., and the pressure was decreased to 4 mm of Hg.The reaction mixture was held at 290° C. and at a pressure of 4 mm of Hgfor 30 minutes. The pressure of the pressure vessel was then increasedto 1 atmosphere using nitrogen gas. The molten polymer was then extrudedfrom the pressure vessel. The cooled, extruded polymer was ground topass a 6-mm screen. The polymer had an inherent viscosity of 0.531 dL/gand a Tg of 105° C. NMR analysis showed that the polymer was composed of76.9 mol % 1,4-cyclohexane-dimethanol residues and 23.1 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues. The polymer had colorvalues of: L*=80.42, a*=−1.28, and b*=5.13.

Example 3J

21.24 lb (49.71 gram-mol) dimethyl terephthalate, 12.61 lb (39.77gram-mol) 1,4-cyclohexanedimethanol, and 6.30 lb (19.88 gram-mol)2,2,4,4-tetramethyl-1,3-cyclobutanediol were reacted together in thepresence of 200 ppm of the catalyst butyltin tris(2-ethylhexanoate). Thereaction was carried out under a nitrogen gas purge in an 18-gallonstainless steel pressure vessel fitted with a condensing column, avacuum system, and a HELICONE-type agitator. With the agitator runningat 25 RPM, the reaction mixture temperature was increased to 250° C. andthe pressure was increased to 20 psig. The reaction mixture was held for2 hours at 250° C. and 20 psig pressure. The pressure was then decreasedto 0 psig at a rate of 3 psig/minute. The temperature of the reactionmixture was then increased to 270° C. and the pressure was decreased to90 mm of Hg. After a 1 hour hold time at 270° C. and 90 mm of Hg, theagitator speed was decreased to 15 RPM, the reaction mixture temperaturewas increased to 290° C., and the pressure was decreased to 4 mm of Hg.When the reaction mixture temperature was 290° C. and the pressure was 4mm of Hg, the pressure of the pressure vessel was immediately increasedto 1 atmosphere using nitrogen gas. The molten polymer was then extrudedfrom the pressure vessel. The cooled, extruded polymer was ground topass a 6-mm screen. The polymer had an inherent viscosity of 0.364 dL/gand a Tg of 98° C. NMR analysis showed that the polymer was composed of77.5 mol % 1,4-cyclohexane-dimethanol residues and 22.5 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues. The polymer had colorvalues of: L*=77.20, a*=−1.47, and b*=4.62.

Example 4

This example illustrates that 2,2,4,4-tetramethyl-1,3-cyclobutanediolcan improve the toughness of PCT-based copolyesters (polyesterscontaining terephthalic acid and 1,4-cyclohexanedimethanol). Polyestersprepared in this example fall comprise more than 25 to less than 40 mol% of 2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Copolyesters based on dimethyl terephthalate,2,2,4,4-tetramethyl-1,3-cyclobutanediol, and 1,4-cyclohexanedimethanol(31/69 cis/trans) were prepared as described below, having thecomposition and properties shown on Table 4. The balance up to 100 mol %of the diol component of the polyesters in Table 4 was1,4-cyclohexanedimethanol (31/69 cis/trans).

Materials were injection molded into both 3.2 mm and 6.4 mm thick barsand subsequently notched for Izod impact testing. The notched Izodimpact strengths were obtained at 23° C. and are reported in Table 4.Density, Tg, and crystallization halftime were measured on the moldedbars. Melt viscosity was measured on pellets at 290° C.

TABLE 4 Compilation of various properties for certain polyesters usefulin the invention Notched Notched Izod of Izod of 3.2 mm 6.4 mm Meltthick thick Crystallization Viscosity Pellet Molded bars at bars atSpecific Halftime from at 1 rad/sec TMCD % cis IV Bar IV 23° C. 23° C.Gravity Tg melt at 170° C. at 290° C. Example mole % TMCD (dl/g) (dl/g)(J/m) (J/m) (g/mL) (° C.) (min) (Poise) A 27 47.8 0.714 0.678 877 8781.178 113 280 8312 B 31 NA 0.667 0.641 807 789 1.174 116 600 6592 NA =Not available.

Example 4A

21.24 lb (49.71 gram-mol) dimethyl terephthalate, 11.82 lb (37.28gram-mol) 1,4-cyclohexanedimethanol, and 6.90 lb (21.77 gram-mol)2,2,4,4-tetramethyl-1,3-cyclobutanediol were reacted together in thepresence of 200 ppm of the catalyst butyltin tris(2-ethylhexanoate). Thereaction was carried out under a nitrogen gas purge in an 18-gallonstainless steel pressure vessel fitted with a condensing column, avacuum system, and a HELICONE-type agitator. With the agitator runningat 25 RPM, the reaction mixture temperature was increased to 250° C. andthe pressure was increased to 20 psig. The reaction mixture was held for2 hours at 250° C. and 20 psig pressure. The pressure was then decreasedto 0 psig at a rate of 3 psig/minute. The temperature of the reactionmixture was then increased to 270° C. and the pressure was decreased to90 mm of Hg. After a 1 hour hold time at 270° C. and 90 mm of Hg, theagitator speed was decreased to 15 RPM, the reaction mixture temperaturewas increased to 290° C., and the pressure was decreased to <1 mm of Hg.The reaction mixture was held at 290° C. and at a pressure of <1 mm ofHg until the power draw to the agitator no longer increased (50minutes). The pressure of the pressure vessel was then increased to 1atmosphere using nitrogen gas. The molten polymer was then extruded fromthe pressure vessel. The cooled, extruded polymer was ground to pass a6-mm screen. The polymer had an inherent viscosity of 0.714 dL/g and aTg of 113° C. NMR analysis showed that the polymer was composed of 73.3mol % 1,4-cyclohexane-dimethanol residues and 26.7 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Example 4B

The polyester of Example 4B was prepared following a procedure similarto the one described for Example 4A. The composition and properties ofthis polyester are shown in Table 4.

Example 5

This example illustrates that 2,2,4,4-tetramethyl-1,3-cyclobutanediolcan improve the toughness of PCT-based copolyesters (polyesterscontaining terephthalic acid and 1,4-cyclohexanedimethanol).

A copolyester based on dimethyl terephthalate,2,2,4,4-tetramethyl-1,3-cyclobutanediol, and 1,4-cyclohexanedimethanolwas prepared as described below, having the composition and propertiesshown on Table 5. The balance up to 100 mol % of the diol component ofthe polyesters in Table 5 was 1,4-cyclohexanedimethanol (31/69cis/trans).

The polyester was injection molded into both 3.2 mm and 6.4 mm thickbars and subsequently notched for Izod impact testing. The notched Izodimpact strengths were obtained at 23° C. and are reported in Table 5.Density, Tg, and crystallization halftime were measured on the moldedbars. Melt viscosity was measured on pellets at 290° C.

TABLE 5 Compilation of various properties for certain polyesters usefulin the invention Notched Notched Izod of Izod of 3.2 mm 6.4 mm Meltthick thick Crystallization Viscosity Pellet Molded bars at bars atSpecific Halftime from at 1 rad/sec TMCD % cis IV Bar IV 23° C. 23° C.Gravity Tg melt at 170° C. at 290° C. Example mole % TMCD (dl/g) (dl/g)(J/m) (J/m) (g/mL) (° C.) (min) (Poise) A 44 46.2 0.657 0.626 727 7341.172 119 NA 9751 NA = Not available.

Example 5A

21.24 lb (49.71 gram-mol) dimethyl terephthalate, 8.84 lb (27.88gram-mol) 1,4-cyclohexanedimethanol, and 10.08 lb (31.77 gram-mol)2,2,4,4-tetramethyl-1,3-cyclobutanediol were reacted together in thepresence of 200 ppm of the catalyst butyltin tris(2-ethylhexanoate). Thereaction was carried out under a nitrogen gas purge in an 18-gallonstainless steel pressure vessel fitted with a condensing column, avacuum system, and a HELICONE-type agitator. With the agitator runningat 25 RPM, the reaction mixture temperature was increased to 250° C. andthe pressure was increased to 20 psig. The reaction mixture was held for2 hours at 250° C. and 20 psig pressure. The pressure was then decreasedto 0 psig at a rate of 3 psig/minute. Then the agitator speed wasdecreased to 15 RPM, the temperature of the reaction mixture was thenincreased to 290° C. and the pressure was decreased to 2 mm of Hg. Thereaction mixture was held at 290° C. and at a pressure of 2 mm of Hguntil the power draw to the agitator no longer increased (80 minutes).The pressure of the pressure vessel was then increased to 1 atmosphereusing nitrogen gas. The molten polymer was then extruded from thepressure vessel. The cooled, extruded polymer was ground to pass a 6-mmscreen. The polymer had an inherent viscosity of 0.657 dL/g and a Tg of119° C. NMR analysis showed that the polymer was composed of 56.3 mol %1,4-cyclohexane-dimethanol residues and 43.7 mol %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues. The polymer had colorvalues of: L*=75.04, a*=−1.82, and b*=6.72.

Example 6 Comparative Example

This example shows data for comparative materials are shown in Table 6.The PC was Makrolon 2608 from Bayer, with a nominal composition of 100mole % bisphenol A residues and 100 mole % diphenyl carbonate residues.Makrolon 2608 has a nominal melt flow rate of 20 grams/10 minutesmeasured at 300 C using a 1.2 kg weight. The PET was Eastar 9921 fromEastman Chemical Company, with a nominal composition of 100 mole %terephthalic acid, 3.5 mole % cyclohexanedimenthanol (CHDM) and 96.5mole % ethylene glycol. The PETG was Eastar 6763 from Eastman ChemicalCompany, with a nominal composition of 100 mole % terephthalic acid, 31mole % cyclohexanedimenthanol (CHDM) and 69 mole % ethylene glycol. ThePCTG was Eastar DN001 from Eastman Chemical Company, with a nominalcomposition of 100 mole % terephthalic acid, 62 mole %cyclohexanedimenthanol (CHDM) and 38 mole % ethylene glycol. The PCTAwas Eastar AN001 from Eastman Chemical Company, with a nominalcomposition of 65 mole % terephthalic acid, 35 mole % isophthalic acidand 100 mole % cyclohexanedimenthanol (CHDM). The Polysulfone was Udel1700 from Solvay, with a nominal composition of 100 mole % bisphenol Aresidues and 100 mole % 4,4-dichlorosulfonyl sulfone residues. Udel 1700has a nominal melt flow rate of 6.5 grams/10 minutes measured at 343 Cusing a 2.16 kg weight. The SAN was Lustran 31 from Lanxess, with anominal composition of 76 weight % styrene and 24 weight %acrylonitrile. Lustran 31 has a nominal melt flow rate of 7.5 grams/10minutes measured at 230 C using a 3.8 kg weight. The examples of theinvention show improved toughness in 6.4 mm thickness bars compared toall of the other resins.

TABLE 6 Compilation of various properties for certain commercialpolymers Notched Notched Izod of Izod of 3.2 mm 6.4 mm thick thickCrystallization Pellet Molded bars at bars at Specific Halftime fromPolymer IV Bar IV 23° C. 23° C. Gravity Tg melt Example name (dl/g)(dl/g) (J/m) (J/m) (g/mL) (° C.) (min) A PC  12 MFR NA 929 108 1.20 146NA B PCTG 0.73 0.696 NB 70 1.23 87 30 at 170° C. C PCTA 0.72 0.702 98 591.20 87 15 at 150° C. D PETG 0.75 0.692 83 59 1.27 80 2500 at 130° C.  EPET 0.76 0.726 45 48 1.33 78 1.5 at 170° C.  F SAN 7.5 MFR NA 21 NA 1.07~110 NA G PSU 6.5 MFR NA 69 NA 1.24 ~190 NA NA = Not available

Example 7

This example illustrates the effect of the amount of2,2,4,4-tetramethyl-1,3-cyclobutanediol used for the preparation of thepolyesters of the invention on the glass transition temperature of thepolyesters. Polyesters prepared in this example comprise from 15 to 25mol % of 2,2,4,4-tetramethyl-1,3-cyclobutanediol residues.

Example 7A to Example 7G

Dimethyl terephthalate, 1,4-cyclohexanedimethanol, and2,2,4,4-tetramethyl-1,3-cyclobutanediol were weighed into a 500-mlsingle neck round bottom flask. NMR analysis on the2,2,4,4-tetramethyl-1,3-cyclobutanediol starting material showed acis/trans ratio of 53/47. The polyesters of this example were preparedwith a 1.2/1 glycol/acid ratio with the entire excess coming from the2,2,4,4-tetramethyl-1,3-cyclobutanediol. Enough dibutyltin oxidecatalyst was added to give 300 ppm tin in the final polymer. The flaskwas under a 0.2 SCFC nitrogen purge with vacuum reduction capability.The flask was immersed in a Belmont metal bath at 200° C. and stirred at200 RPM after the reactants had melted. After about 2.5 hours, thetemperature was raised to 210° C. and these conditions were held for anadditional 2 hours. The temperature was raised to 285° C. (inapproximately 25 minutes) and the pressure was reduced to 0.3 mm of Hgover a period of 5 minutes. The stirring was reduced as the viscosityincreased, with 15 RPM being the minimum stirring used. The totalpolymerization time was varied to attain the target inherentviscosities. After the polymerization was complete, the Belmont metalbath was lowered and the polymer was allowed to cool to below its glasstransition temperature. After about 30 minutes, the flask was reimmersedin the Belmont metal bath (the temperature had been increased to 295° C.during this 30 minute wait) and the polymer mass was heated until itpulled away from the glass flask. The polymer mass was stirred at midlevel in the flask until the polymer had cooled. The polymer was removedfrom the flask and ground to pass a 3 mm screen. Variations to thisprocedure were made to produce the copolyesters described below with atargeted composition of 20 mol %.

Inherent viscosities were measured as described in the “MeasurementMethods” section above. The compositions of the polyesters weredetermined by ¹H NMR as explained before in the Measurement Methodssection. The glass transition temperatures were determined by DSC, usingthe second heat after quench at a rate of 20° C./min.

Example 7H to Example 7Q

These polyesters were prepared by carrying out the ester exchange andpolycondensation reactions in separate stages. The ester exchangeexperiments were conducted in a continuous temperature rise (CTR)reactor. The CTR was a 3000 ml glass reactor equipped with a singleshaft impeller blade agitator, covered with an electric heating mantleand fitted with a heated packed reflux condenser column. The reactor wascharged with 777 g (4 moles) of dimethyl terephthalate, 230 g (1.6moles) of 2,2,4,4-tetramethyl-1,3,-cyclobutanediol, 460.8 g (3.2 moles)of cyclohexane dimethanol and 1.12 g of butyltin tris-2-ethylhexanoate(such that there will be 200 ppm tin metal in the final polymer). Theheating mantle was set manually to 100% output. The set points and datacollection were facilitated by a Camile process control system. Once thereactants were melted, stirring was initiated and slowly increased to250 rpm. The temperature of the reactor gradually increased with runtime. The weight of methanol collected was recorded via balance. Thereaction was stopped when methanol evolution stopped or at apre-selected lower temperature of 260° C. The oligomer was dischargedwith a nitrogen purge and cooled to room temperature. The oligomer wasfrozen with liquid nitrogen and broken into pieces small enough to beweighed into a 500 ml round bottom flask.

In the polycondensation reactions, a 500 ml round bottom flask wascharged with approximately 150 g of the oligomer prepared above. Theflask was equipped with a stainless steel stirrer and polymer head. Theglassware was set up on a half mole polymer rig and the Camile sequencewas initiated. The stirrer was positioned one full turn from the flaskbottom once the oligomer melted. The temperature/pressure/stir ratesequence controlled by the Camile software for each example is reportedin the following tables.

Camile Sequence for Example 7H and Example 7I

Time Temp Vacuum Stir Stage (min) (° C.) (torr) (rpm) 1 5 245 760 0 2 5245 760 50 3 30 265 760 50 4 3 265 90 50 5 110 290 90 50 6 5 290 6 25 7110 290 6 25

Camile Sequence for Example 7N to Example 7Q

Time Temp Vacuum Stir Stage (min) (° C.) (torr) (rpm) 1 5 245 760 0 2 5245 760 50 3 30 265 760 50 4 3 265 90 50 5 110 290 90 50 6 5 290 3 25 7110 290 3 25

Camile Sequence for Example 7K and Example 7L

Time Temp Vacuum Stir Stage (min) (° C.) (torr) (rpm) 1 5 245 760 0 2 5245 760 50 3 30 265 760 50 4 3 265 90 50 5 110 290 90 50 6 5 290 2 25 7110 290 2 25

Camile Sequence for Example 7J and Example 7M

Time Temp Vacuum Stir Stage (min) (° C.) (torr) (rpm) 1 5 245 760 0 2 5245 760 50 3 30 265 760 50 4 3 265 90 50 5 110 290 90 50 6 5 290 1 25 7110 290 1 25

The resulting polymers were recovered from the flask, chopped using ahydraulic chopper, and ground to a 6 mm screen size. Samples of eachground polymer were submitted for inherent viscosity in 60/40 (wt/wt)phenol/tetrachloroethane at a concentration of 0.5 g/100 ml at 25° C.,catalyst level (Sn) by x-ray fluorescence, and color (L*, a*, b*) bytransmission spectroscopy. Polymer composition was obtained by ¹H NMR.Samples were submitted for Thermal stability and melt viscosity testingusing a Rheometrics Mechanical Spectrometer (RMS-800).

The table below shows the experimental data for the polyesters of thisexample. The data shows that an increase in the level of2,2,4,4-tetramethyl-1,3-cyclobutanediol raises the glass transitiontemperature in an almost linear fashion, for a constant inherentviscosity. FIG. 3 also shows the dependence of Tg on composition andinherent viscosity.

TABLE 7 Glass transition temperature as a function of inherent viscosityand composition η_(o) at η_(o) at η_(o) at % cis 260° C. 275° C. 290° C.Example mol % TMCD TMCD IV (dL/g) T_(g) (° C.) (Poise) (Poise) (Poise) A20 51.4 0.72 109 11356 19503 5527 B 19.1 51.4 0.60 106 6891 3937 2051 C19 53.2 0.64 107 8072 4745 2686 D 18.8 54.4 0.70 108 14937 8774 4610 E17.8 52.4 0.50 103 3563 1225 883 F 17.5 51.9 0.75 107 21160 10877 5256 G17.5 52 0.42 98 NA NA NA H 22.8 53.5 0.69 109 NA NA NA I 22.7 52.2 0.68108 NA NA NA J 23.4 52.4 0.73 111 NA NA NA K 23.3 52.9 0.71 111 NA NA NAL 23.3 52.4 0.74 112 NA NA NA M 23.2 52.5 0.74 112 NA NA NA N 23.1 52.50.71 111 NA NA NA O 22.8 52.4 0.73 112 NA NA NA P 22.7 53 0.69 112 NA NANA Q 22.7 52 0.70 111 NA NA NA NA = Not available

Example 8

This example illustrates the effect of the amount of2,2,4,4-tetramethyl-1,3-cyclobutanediol used for the preparation of thepolyesters of the invention on the glass transition temperature of thepolyesters. Polyesters prepared in this example fall comprise more than25 to less than 40 mol % of 2,2,4,4-tetramethyl-1,3-cyclobutanediolresidues.

Dimethyl terephthalate, 1,4-cyclohexanedimethanol, and2,2,4,4-tetramethyl-1,3-cyclobutanediol were weighed into a 500-mlsingle neck round bottom flask. NMR analysis on the2,2,4,4-tetramethyl-1,3-cyclobutanediol starting material showed acis/trans ratio of 53/47. The polyesters of this example were preparedwith a 1.2/1 glycol/acid ratio with the entire excess coming from the2,2,4,4-tetramethyl-1,3-cyclobutanediol. Enough dibutyltin oxidecatalyst was added to give 300 ppm tin in the final polymer. The flaskwas under a 0.2 SCFC nitrogen purge with vacuum reduction capability.The flask was immersed in a Belmont metal bath at 200° C. and stirred at200 RPM after the reactants had melted. After about 2.5 hours, thetemperature was raised to 210° C. and these conditions were held for anadditional 2 hours. The temperature was raised to 285° C. (inapproximately 25 minutes) and the pressure was reduced to 0.3 mm of Hgover a period of 5 minutes. The stirring was reduced as the viscosityincreased, with 15 RPM being the minimum stirring used. The totalpolymerization time was varied to attain the target inherentviscosities. After the polymerization was complete, the Belmont metalbath was lowered and the polymer was allowed to cool to below its glasstransition temperature. After about 30 minutes, the flask was reimmersedin the Belmont metal bath (the temperature had been increased to 295° C.during this 30 minute wait) and the polymer mass was heated until itpulled away from the glass flask. The polymer mass was stirred at midlevel in the flask until the polymer had cooled. The polymer was removedfrom the flask and ground to pass a 3 mm screen. Variations to thisprocedure were made to produce the copolyesters described below with atargeted composition of 32 mol %.

Inherent viscosities were measured as described in the “MeasurementMethods” section above. The compositions of the polyesters weredetermined by ¹H NMR as explained before in the Measurement Methodssection. The glass transition temperatures were determined by DSC, usingthe second heat after quench at a rate of 20° C./min.

The table below shows the experimental data for the polyesters of thisexample. FIG. 3 also shows the dependence of Tg on composition andinherent viscosity. The data shows that an increase in the level of2,2,4,4-tetramethyl-1,3-cyclobutanediol raises the glass transitiontemperature in an almost linear fashion, for a constant inherentviscosity.

TABLE 8 Glass transition temperature as a function of inherent viscosityand composition η_(o) at η_(o) at η_(o) at % cis 260° C. 275° C. 290° C.Example mol % TMCD TMCD IV (dL/g) T_(g) (° C.) (Poise) (Poise) (Poise) A32.2 51.9 0.71 118 29685 16074 8522 B 31.6 51.5 0.55 112 5195 2899 2088C 31.5 50.8 0.62 112 8192 4133 2258 D 30.7 50.7 0.54 111 4345 2434 1154E 30.3 51.2 0.61 111 7929 4383 2261 F 30.0 51.4 0.74 117 31476 178648630 G 29.0 51.5 0.67 112 16322 8787 4355 H 31.1 51.4 0.35 102 NA NA NANA = Not available

Example 9

This example illustrates the effect of the amount of2,2,4,4-tetramethyl-1,3-cyclobutanediol used for the preparation of thepolyesters of the invention on the glass transition temperature of thepolyesters. Polyesters prepared in this example comprise2,2,4,4-tetramethyl-1,3-cyclobutanediol residues in an amount of 40 mol% or greater.

Examples A to C

These polyesters were prepared by carrying out the ester exchange andpolycondensation reactions in separate stages. The ester exchangeexperiments were conducted in a continuous temperature rise (CTR)reactor. The CTR was a 3000 ml glass reactor equipped with a singleshaft impeller blade agitator, covered with an electric heating mantleand fitted with a heated packed reflux condenser column. The reactor wascharged with 777 g of dimethyl terephthalate, 375 g of2,2,4,4-tetramethyl-1,3,-cyclobutanediol, 317 g of cyclohexanedimethanol and 1.12 g of butyltin tris-2-ethylhexanoate (such that therewill be 200 ppm tin metal in the final polymer). The heating mantle wasset manually to 100% output. The set points and data collection werefacilitated by a Camile process control system. Once the reactants weremelted, stirring was initiated and slowly increased to 250 rpm. Thetemperature of the reactor gradually increased with run time. The weightof methanol collected was recorded via balance. The reaction was stoppedwhen methanol evolution stopped or at a pre-selected lower temperatureof 260° C. The oligomer was discharged with a nitrogen purge and cooledto room temperature. The oligomer was frozen with liquid nitrogen andbroken into pieces small enough to be weighed into a 500 ml round bottomflask.

In the polycondensation reactions, a 500 ml round bottom flask wascharged with 150 g of the oligomer prepared above. The flask wasequipped with a stainless steel stirrer and polymer head. The glasswarewas set up on a half mole polymer rig and the Camile sequence wasinitiated. The stirrer was positioned one full turn from the flaskbottom once the oligomer melted. The temperature/pressure/stir ratesequence controlled by the Camile software for these examples isreported in the following table, unless otherwise specified below.

Vacuum Stage Time (min) Temp (° C.) (torr) Stir (rpm) Camile Sequencefor Polycondensation Reactions 1 5 245 760 0 2 5 245 760 50 3 30 265 76050 4 3 265 90 50 5 110 290 90 50 6 5 290 6 25 7 110 290 6 25 CamileSequence for Examples A and B 1 5 245 760 0 2 5 245 760 50 3 30 265 76050 4 3 265 90 50 5 110 290 90 50 6 5 290 6 25 7 80 290 6 25

For Example C, the same sequence in the preceding table was used, exceptthe time was 50 min in Stage 7.

The resulting polymers were recovered from the flask, chopped using ahydraulic chopper, and ground to a 6 mm screen size. Samples of eachground polymer were submitted for inherent viscosity in 60/40 (wt/wt)phenol/tetrachloroethane at a concentration of 0.5 g/100 ml at 25° C.,catalyst level (Sn) by x-ray fluorescence, and color (L*, a*, b*) bytransmission spectroscopy. Polymer composition was obtained by 1H NMR.Samples were submitted for Thermal stability and melt viscosity testingusing a Rheometrics Mechanical Spectrometer (RMS-800).

Examples D to K and M

The polyesters of these examples were prepared as described above forExamples A to C, except that the target tin amount in the final polymerwas 150 ppm for examples AD to K and M. The following tables describethe temperature/pressure/stir rate sequences controlled by the Camilesoftware for these examples.

Camile Sequence for Examples D, F, and H

Vacuum Stage Time (min) Temp (° C.) (torr) Stir (rpm) 1 5 245 760 0 2 5245 760 50 3 30 265 760 50 4 3 265 400 50 5 110 290 400 50 6 5 290 8 507 110 295 8 50

For Example D, the stirrer was turned to 25 rpm with 95 min left inStage 7.

Camile Sequence for Example E

Vacuum Stage Time (min) Temp (° C.) (torr) Stir (rpm) 1 10 245 760 0 2 5245 760 50 3 30 283 760 50 4 3 283 175 50 5 5 283 5 50 6 5 283 1.2 50 771 285 1.2 50

For Example K, the same sequence in the preceding table was used, exceptthe time was 75 min in Stage 7.

Camile Sequence for Example G

Vacuum Stage Time (min) Temp (° C.) (torr) Stir (rpm) 1 10 245 760 0 2 5245 760 50 3 30 285 760 50 4 3 285 175 50 5 5 285 5 50 6 5 285 4 50 7220 290 4 50

Camile Sequence for Example I

Vacuum Stage Time (min) Temp (° C.) (torr) Stir (rpm) 1 5 245 760 0 2 5245 760 50 3 30 265 760 50 4 3 265 90 50 5 110 285 90 50 6 5 285 6 50 770 290 6 50

Camile Sequence for Example J

Vacuum Stage Time (min) Temp (° C.) (torr) Stir (rpm) 1 5 245 760 0 2 5245 760 50 3 30 265 760 50 4 3 265 90 50 5 110 290 90 50 6 5 290 6 25 7110 295 6 25

Examples L and K

Dimethyl terephthalate, 1,4-cyclohexanedimethanol, and2,2,4,4-tetramethyl-1,3-cyclobutanediol were weighed into a 500-mlsingle neck round bottom flask. The polyesters of this example wereprepared with a 1.2/1 glycol/acid ratio with the entire excess comingfrom the 2,2,4,4-tetramethyl-1,3-cyclobutanediol. Enough dibutyltinoxide catalyst was added to give 300 ppm tin in the final polymer. Theflask was under a 0.2 SCFC nitrogen purge with vacuum reductioncapability. The flask was immersed in a Belmont metal bath at 200° C.and stirred at 200 RPM after the reactants had melted. After about 2.5hours, the temperature was raised to 210° C. and these conditions wereheld for an additional 2 hours. The temperature was raised to 285° C.(in approximately 25 minutes) and the pressure was reduced to 0.3 mm ofHg over a period of 5 minutes. The stirring was reduced as the viscosityincreased, with 15 RPM being the minimum stirring used. The totalpolymerization time was varied to attain the target inherentviscosities. After the polymerization was complete, the Belmont metalbath was lowered and the polymer was allowed to cool to below its glasstransition temperature. After about 30 minutes, the flask was reimmersedin the Belmont metal bath (the temperature had been increased to 295° C.during this 30 minute wait) and the polymer mass was heated until itpulled away from the glass flask. The polymer mass was stirred at midlevel in the flask until the polymer had cooled. The polymer was removedfrom the flask and ground to pass a 3 mm screen. Variations to thisprocedure were made to produce the copolyesters described below with atargeted composition of 45 mol %.

Inherent viscosities were measured as described in the “MeasurementMethods” section above. The compositions of the polyesters weredetermined by ¹H NMR as explained before in the Measurement Methodssection. The glass transition temperatures were determined by DSC, usingthe second heat after quench at a rate of 20° C./min.

The table below shows the experimental data for the polyesters of thisexample. The data shows that an increase in the level of2,2,4,4-tetramethyl-1,3-cyclobutanediol raises the glass transitiontemperature in an almost linear fashion, for a constant inherentviscosity. FIG. 3 also shows the dependence of Tg on composition andinherent viscosity.

TABLE 9 Glass transition temperature as a function of inherent viscosityand composition η_(o) at η_(o) at η_(o) at % cis 260° C. 275° C. 290° C.Example mol % TMCD TMCD IV (dL/g) T_(g) (° C.) (Poise) (Poise) (Poise) A44.2 36.4 0.49 118 NA NA NA B 44.3 36.3 0.51 119 NA NA NA C 44.4 35.60.55 118 NA NA NA D 46.3 52.4 0.52 NA NA NA NA E 45.7 50.9 0.54 NA NA NANA F 46.3 52.6 0.56 NA NA NA NA G 46 50.6 0.56 NA NA NA NA H 46.5 51.80.57 NA NA NA NA I 45.6 51.2 0.58 NA NA NA NA J 46 51.9 0.58 NA NA NA NAK 45.5 51.2 0.59 NA NA NA NA L 46.1 49.6 0.383 117 NA NA 387 K 45.6 50.50.325 108 NA NA NA M 47.2 NA 0.48 NA NA NA NA NA = Not available

Example 10

This example illustrates the effect of the predominance of the type of2,2,4,4-tetramethyl-1,3-cyclobutanediol isomer (cis or trans) on theglass transition temperature of the polyester.

Dimethyl terephthalate, 1,4-cyclohexanedimethanol, and2,2,4,4-tetramethyl-1,3-cyclobutanediol were weighed into a 500-mlsingle neck round bottom flask. The polyesters of this example wereprepared with a 1.2/1 glycol/acid ratio with the entire excess comingfrom the 2,2,4,4-tetramethyl-1,3-cyclobutanediol. Enough dibutyltinoxide catalyst was added to give 300 ppm tin in the final polymer. Theflask was under a 0.2 SCFC nitrogen purge with vacuum reductioncapability. The flask was immersed in a Belmont metal bath at 200° C.and stirred at 200 RPM after the reactants had melted. After about 2.5hours, the temperature was raised to 210° C. and these conditions wereheld for an additional 2 hours. The temperature was raised to 285° C.(in approximately 25 minutes) and the pressure was reduced to 0.3 mm ofHg over a period of 5 minutes. The stirring was reduced as the viscosityincreased, with 15 RPM being the minimum stirring used. The totalpolymerization time was varied to attain the target inherentviscosities. After the polymerization was complete, the Belmont metalbath was lowered and the polymer was allowed to cool to below its glasstransition temperature. After about 30 minutes, the flask was reimmersedin the Belmont metal bath (the temperature had been increased to 295° C.during this 30 minute wait) and the polymer mass was heated until itpulled away from the glass flask. The polymer mass was stirred at midlevel in the flask until the polymer had cooled. The polymer was removedfrom the flask and ground to pass a 3 mm screen. Variations to thisprocedure were made to produce the copolyesters described below with atargeted composition of 45 mol %.

Inherent viscosities were measured as described in the “MeasurementMethods” section above. The compositions of the polyesters weredetermined by ¹H NMR as explained before in the Measurement Methodssection. The glass transition temperatures were determined by DSC, usingthe second heat after quench at a rate of 20° C./min.

The table below shows the experimental data for the polyesters of thisExample. The data shows that cis 2,2,4,4-tetramethyl-1,3-cyclobutanediolis approximately twice as effective as trans2,2,4,4-tetramethyl-1,3-cyclobutanediol at increasing the glasstransition temperature for a constant inherent viscosity.

TABLE 10 Effect of 2,2,4,4-tetramethyl-1,3-cyclobutanediol cis/transcomposition on T_(g) η_(o) at η_(o) at η_(o) at Ex- mol % IV T_(g) 260°C. 275° C. 290° C. % cis ample TMCD (dL/g) (° C.) (Poise) (Poise)(Poise) TMCD A 45.8 0.71 119 N.A. N.A. N.A. 4.1 B 43.2 0.72 122 N.A.N.A. N.A. 22.0 C 46.8 0.57 119 26306 16941 6601 22.8 D 43.0 0.67 12555060 36747 14410 23.8 E 43.8 0.72 127 101000 62750 25330 24.5 F 45.90.533 119 11474 6864 2806 26.4 G 45.0 0.35 107 N.A. N.A. N.A. 27.2 H41.2 0.38 106 1214 757 N.A. 29.0 I 44.7 0.59 123 N.A. N.A. N.A. 35.4 J44.4 0.55 118 N.A. N.A. N.A. 35.6 K 44.3 0.51 119 N.A. N.A. N.A. 36.3 L44.0 0.49 128 N.A. N.A. N.A. 71.7 M 43.6 0.52 128 N.A. N.A. N.A. 72.1 N43.6 0.54 127 N.A. N.A. N.A. 72.3 O 41.5 0.58 133 15419 10253 4252 88.7P 43.8 0.57 135 16219 10226 4235 89.6 Q 41.0 0.33 120 521 351 2261 90.4R 43.0 0.56 134 N.A. N.A. N.A. 90.6 S 43.0 0.49 132 7055 4620 2120 90.6T 43.1 0.55 134 12970 8443 3531 91.2 U 45.9 0.52 137 N.A. N.A. N.A. 98.1NA = not available

Example 11 Comparative Example

This example illustrates that a polyester based on 100%2,2,4,4-tetramethyl-1,3-cyclobutanediol has a slow crystallizationhalf-time.

A polyester based solely on terephthalic acid and2,2,4,4-tetramethyl-1,3-cyclobutanediol was prepared in a method similarto the method described in Example 1A with the properties shown on Table11. This polyester was made with 300 ppm dibutyl tin oxide. Thetrans/cis ratio of the 2,2,4,4-tetramethyl-1,3-cyclobutanediol was65/35.

Films were pressed from the ground polymer at 320° C. Crystallizationhalf-time measurements from the melt were made at temperatures from 220to 250° C. at 10° C. increments and are reported in Table 11. Thefastest crystallization half-time for the sample was taken as theminimum value of crystallization half-time as a function of temperature.The fastest crystallization half-time of this polyester is around 1300minutes. This value contrasts with the fact that the polyester (PCT)based solely on terephthalic acid and 1,4-cyclohexanedimethanol (nocomonomer modification) has an extremely short crystallization half-time(<1 min) as shown in FIG. 1.

TABLE 11 Crystallization Half-times (min) at at at at Comonomer 220° C.230° C. 240° C. 250° C. (mol %) IV (dl/g) T_(g) (° C.) T_(max) (° C.)(min) (min) (min) (min) 100 mol % F 0.63 170.0 330 3291 3066 1303 1888where: F is 2,2,4,4-Tetramethyl-1,3-cyclobutanediol (65/35 Trans/Cis)

Example 12

Sheets comprising a polyester that had been prepared with a targetcomposition of 100 mole % terephthalic acid residues, 80 mole %1,4-cyclohexanedimethanol residues, and 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues were produced using a3.5 inch single screw extruder. A sheet was extruded continuously,gauged to a thickness of 177 mil and then various sheets were sheared tosize. Inherent viscosity and glass transition temperature were measuredon one sheet. The sheet inherent viscosity was measured to be 0.69 dl/g.The glass transition temperature of the sheet was measured to be 106° C.Sheets were then conditioned at 50% relative humidity and 60° C. for 2weeks. Sheets were subsequently thermoformed into a female mold having adraw ratio of 2.5:1 using a Brown thermoforming machine. Thethermoforming oven heaters were set to 70/60/60% output using top heatonly. Sheets were left in the oven for various amounts of time in orderto determine the effect of sheet temperature on the part quality asshown in the table below. Part quality was determined by measuring thevolume of the thermoformed part, calculating the draw, and visuallyinspecting the thermoformed part. The draw was calculated as the partvolume divided by the maximum part volume achieved in this set ofexperiments (Example G). The thermoformed part was visually inspectedfor any blisters and the degree of blistering rated as none (N), low(L), or high (H). The results below demonstrate that these thermoplasticsheets with a glass transition temperature of 106° C. can bethermoformed under the conditions shown below, as evidenced by thesesheets having at least 95% draw and no blistering, without predrying thesheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 86 145 50164 N B 100 150 500 63 N C 118 156 672 85 N D 135 163 736 94 N E 143 166760 97 N F 150 168 740 94 L G 159 172 787 100 L

Example 13

Sheets comprising a polyester that had been prepared with a targetcomposition of 100 mole % terephthalic acid residues, 80 mole %1,4-cyclohexanedimethanol residues, and 20 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues were produced using a3.5 inch single screw. A sheet was extruded continuously, gauged to athickness of 177 mil and then various sheets were sheared to size.Inherent viscosity and glass transition temperature were measured on onesheet. The sheet inherent viscosity was measured to be 0.69 dl/g. Theglass transition temperature of the sheet was measured to be 106° C.Sheets were then conditioned at 100% relative humidity and 25° C. for 2weeks. Sheets were subsequently thermoformed into a female mold having adraw ratio of 2.5:1 using a Brown thermoforming machine. Thethermoforming oven heaters were set to 60/40/40% output using top heatonly. Sheets were left in the oven for various amounts of time in orderto determine the effect of sheet temperature on the part quality asshown in the table below. Part quality was determined by measuring thevolume of the thermoformed part, calculating the draw, and visuallyinspecting the thermoformed part. The draw was calculated as the partvolume divided by the maximum part volume achieved in this set ofexperiments (Example G). The thermoformed part was visually inspectedfor any blisters and the degree of blistering rated as none (N), low(L), or high (H). The results below demonstrate that these thermoplasticsheets with a glass transition temperature of 106° C. can bethermoformed under the conditions shown below, as evidenced by theproduction of sheets having at least 95% draw and no blistering, withoutpredrying the sheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 141 154 39453 N B 163 157 606 82 N C 185 160 702 95 N D 195 161 698 95 N E 215 163699 95 L F 230 168 705 96 L G 274 174 737 100 H H 275 181 726 99 H

Example 14 Comparative Example

Sheets consisting of Kelvx 201 were produced using a 3.5 inch singlescrew extruder. Kelvx is a blend consisting of 69.85% PCTG (Eastar fromEastman Chemical Co. having 100 mole % terephthalic acid residues, 62mole % 1,4-cyclohexanedimethanol residues, and 38 mole % ethylene glycolresidues); 30% PC (bisphenol A polycarbonate); and 0.15% Weston 619(stabilizer sold by Crompton Corporation). A sheet was extrudedcontinuously, gauged to a thickness of 177 mil and then various sheetswere sheared to size. The glass transition temperature was measured onone sheet and was 100° C. Sheets were then conditioned at 50% relativehumidity and 60° C. for 2 weeks. Sheets were subsequently thermoformedinto a female mold having a draw ratio of 2.5:1 using a Brownthermoforming machine. The thermoforming oven heaters were set to70/60/60% output using top heat only. Sheets were left in the oven forvarious amounts of time in order to determine the effect of sheettemperature on the part quality as shown in the table below. Partquality was determined by measuring the volume of the thermoformed part,calculating the draw, and visually inspecting the thermoformed part. Thedraw was calculated as the part volume divided by the maximum partvolume achieved in this set of experiments (Example E). The thermoformedpart was visually inspected for any blisters and the degree ofblistering rated as none (N), low (L), or high (H). The results belowdemonstrate that these thermoplastic sheets with a glass transitiontemperature of 100° C. can be thermoformed under the conditions shownbelow, as evidenced by the production of sheets having at least 95% drawand no blistering, without predrying the sheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 90 146 58275 N B 101 150 644 83 N C 111 154 763 98 N D 126 159 733 95 N E 126 159775 100 N F 141 165 757 98 N G 148 168 760 98 L

Example 15 Comparative Example

Sheets consisting of Kelvx 201 were produced using a 3.5 inch singlescrew extruder. A sheet was extruded continuously, gauged to a thicknessof 177 mil and then various sheets were sheared to size. The glasstransition temperature was measured on one sheet and was 100° C. Sheetswere then conditioned at 100% relative humidity and 25° C. for 2 weeks.Sheets were subsequently thermoformed into a female mold having a drawratio of 2.5:1 using a Brown thermoforming machine. The thermoformingoven heaters were set to 60/40/40% output using top heat only. Sheetswere left in the oven for various amounts of time in order to determinethe effect of sheet temperature on the part quality as shown in thetable below. Part quality was determined by measuring the volume of thethermoformed part, calculating the draw, and visually inspecting thethermoformed part. The draw was calculated as the part volume divided bythe maximum part volume achieved in this set of experiments (Example H).The thermoformed part was visually inspected for any blisters and thedegree of blistering rated as none (N), low (L), or high (H). Theresults below demonstrate that these thermoplastic sheets with a glasstransition temperature of 100° C. can be thermoformed under theconditions shown below, as evidenced by the production of sheets havinggreater than 95% draw and no blistering, without predrying the sheetsprior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 110 143 18525 N B 145 149 529 70 N C 170 154 721 95 N D 175 156 725 96 N E 185 157728 96 N F 206 160 743 98 L G 253 NR 742 98 H H 261 166 756 100 H NR =Not recorded

Example 16 Comparative Example

Sheets consisting of PCTG 25976 (100 mole % terephthalic acid residues,62 mole % 1,4-cyclohexanedimethanol residues, and 38 mole % ethyleneglycol residues) were produced using a 3.5 inch single screw extruder. Asheet was extruded continuously, gauged to a thickness of 118 mil andthen various sheets were sheared to size. The glass transitiontemperature was measured on one sheet and was 87° C. Sheets were thenconditioned at 50% relative humidity and 60° C. for 4 weeks. Themoisture level was measured to be 0.17 wt %. Sheets were subsequentlythermoformed into a female mold having a draw ratio of 2.5:1 using aBrown thermoforming machine. The thermoforming oven heaters were set to70/60/60% output using top heat only. Sheets were left in the oven forvarious amounts of time in order to determine the effect of sheettemperature on the part quality as shown in the table below. Partquality was determined by measuring the volume of the thermoformed part,calculating the draw, and visually inspecting the thermoformed part. Thedraw was calculated as the part volume divided by the maximum partvolume achieved in this set of experiments (Example A). The thermoformedpart was visually inspected for any blisters and the degree ofblistering rated as none (N), low (L), or high (H). The results belowdemonstrate that these thermoplastic sheets with a glass transitiontemperature of 87° C. can be thermoformed under the conditions shownbelow, as evidenced by the production of sheets having greater than 95%draw and no blistering, without predrying the sheets prior tothermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 102 183 816100 N B 92 171 811 99 N C 77 160 805 99 N D 68 149 804 99 N E 55 143 79097 N F 57 138 697 85 N

Example 17 Comparative Example

A miscible blend consisting of 20 wt % Teijin L-1250 polycarbonate (abisphenol-A polycarbonate), 79.85 wt % PCTG 25976, and 0.15 wt % Weston619 was produced using a 1.25 inch single screw extruder. Sheetsconsisting of the blend were then produced using a 3.5 inch single screwextruder. A sheet was extruded continuously, gauged to a thickness of118 mil and then various sheets were sheared to size. The glasstransition temperature was measured on one sheet and was 94° C. Sheetswere then conditioned at 50% relative humidity and 60° C. for 4 weeks.The moisture level was measured to be 0.25 wt %. Sheets weresubsequently thermoformed into a female mold having a draw ratio of2.5:1 using a Brown thermoforming machine. The thermoforming ovenheaters were set to 70/60/60% output using top heat only. Sheets wereleft in the oven for various amounts of time in order to determine theeffect of sheet temperature on the part quality as shown in the tablebelow. Part quality was determined by measuring the volume of thethermoformed part, calculating the draw, and visually inspecting thethermoformed part. The draw was calculated as the part volume divided bythe maximum part volume achieved in this set of experiments (Example A).The thermoformed part was visually inspected for any blisters and thedegree of blistering rated as none (N), low (L), or high (H). Theresults below demonstrate that these thermoplastic sheets with a glasstransition temperature of 94° C. can be thermoformed under theconditions shown below, as evidenced by the production of sheets havinggreater than 95% draw and no blistering, without predrying the sheetsprior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 92 184 844100 H B 86 171 838 99 N C 73 160 834 99 N D 58 143 787 93 N E 55 143 66579 N

Example 18 Comparative Example

A miscible blend consisting of 30 wt % Teijin L-1250 polycarbonate,69.85 wt % PCTG 25976, and 0.15 wt % Weston 619 was produced using a1.25 inch single screw extruder. Sheets consisting of the blend werethen produced using a 3.5 inch single screw extruder. A sheet wasextruded continuously, gauged to a thickness of 118 mil and then varioussheets were sheared to size. The glass transition temperature wasmeasured on one sheet and was 99° C. Sheets were then conditioned at 50%relative humidity and 60° C. for 4 weeks. The moisture level wasmeasured to be 0.25 wt %. Sheets were subsequently thermoformed into afemale mold having a draw ratio of 2.5:1 using a Brown thermoformingmachine. The thermoforming oven heaters were set to 70/60/60% outputusing top heat only. Sheets were left in the oven for various amounts oftime in order to determine the effect of sheet temperature on the partquality as shown in the table below. Part quality was determined bymeasuring the volume of the thermoformed part, calculating the draw, andvisually inspecting the thermoformed part. The draw was calculated asthe part volume divided by the maximum part volume achieved in this setof experiments (Example A). The thermoformed part was visually inspectedfor any blisters and the degree of blistering rated as none (N), low(L), or high (H). The results below demonstrate that these thermoplasticsheets with a glass transition temperature of 99° C. can be thermoformedunder the conditions shown below, as evidenced by the production ofsheets having greater than 95% draw and no blistering, without predryingthe sheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 128 194 854100 H B 98 182 831 97 L C 79 160 821 96 N D 71 149 819 96 N E 55 145 78592 N F 46 143 0 0 NA G 36 132 0 0 NA NA = not applicable. A value ofzero indicates that the sheet was not formed because it did not pullinto the mold (likely because it was too cold).

Example 19 Comparative Example

A miscible blend consisting of 40 wt % Teijin L-1250 polycarbonate,59.85 wt % PCTG 25976, and 0.15 wt % Weston 619 was produced using a1.25 inch single screw extruder. Sheets consisting of the blend werethen produced using a 3.5 inch single screw extruder. A sheet wasextruded continuously, gauged to a thickness of 118 mil and then varioussheets were sheared to size. The glass transition temperature wasmeasured on one sheet and was 105° C. Sheets were then conditioned at50% relative humidity and 60° C. for 4 weeks. The moisture level wasmeasured to be 0.265 wt %. Sheets were subsequently thermoformed into afemale mold having a draw ratio of 2.5:1 using a Brown thermoformingmachine. The thermoforming oven heaters were set to 70/60/60% outputusing top heat only. Sheets were left in the oven for various amounts oftime in order to determine the effect of sheet temperature on the partquality as shown in the table below. Part quality was determined bymeasuring the volume of the thermoformed part, calculating the draw, andvisually inspecting the thermoformed part. The draw was calculated asthe part volume divided by the maximum part volume achieved in this setof experiments (Examples 8A to 8E). The thermoformed part was visuallyinspected for any blisters and the degree of blistering rated as none(N), low (L), or high (H). The results below demonstrate that thesethermoplastic sheets with a glass transition temperature of 105° C. canbe thermoformed under the conditions shown below, as evidenced by theproduction of sheets having greater than 95% draw and no blistering,without predrying the sheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 111 191 828100 H B 104 182 828 100 H C 99 179 827 100 N D 97 177 827 100 N E 78 160826 100 N F 68 149 759 92 N G 65 143 606 73 N

Example 20 Comparative Example

A miscible blend consisting of 50 wt % Teijin L-1250 polycarbonate,49.85 wt % PCTG 25976, and 0.15 wt % Weston 619 was produced using a1.25 inch single screw extruder. A sheet was extruded continuously,gauged to a thickness of 118 mil and then various sheets were sheared tosize. The glass transition temperature was measured on one sheet and was111° C. Sheets were then conditioned at 50% relative humidity and 60° C.for 4 weeks. The moisture level was measured to be 0.225 wt %. Sheetswere subsequently thermoformed into a female mold having a draw ratio of2.5:1 using a Brown thermoforming machine. The thermoforming ovenheaters were set to 70/60/60% output using top heat only. Sheets wereleft in the oven for various amounts of time in order to determine theeffect of sheet temperature on the part quality as shown in the tablebelow. Part quality was determined by measuring the volume of thethermoformed part, calculating the draw, and visually inspecting thethermoformed part. The draw was calculated as the part volume divided bythe maximum part volume achieved in this set of experiments (Examples Ato D). The thermoformed part was visually inspected for any blisters andthe degree of blistering rated as none (N), low (L), or high (H). Theresults below demonstrate that these thermoplastic sheets with a glasstransition temperature of 111° C. can be thermoformed under theconditions shown below, as evidenced by the production of sheets havinggreater than 95% draw and no blistering, without predrying the sheetsprior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 118 192 815100 H B 99 182 815 100 H C 97 177 814 100 L D 87 171 813 100 N E 80 160802 98 N F 64 154 739 91 N G 60 149 0 0 NA NA = not applicable. A valueof zero indicates that the sheet was not formed because it did not pullinto the mold (likely because it was too cold).

Example 21 Comparative Example

A miscible blend consisting of 60 wt % Teijin L-1250 polycarbonate,39.85 wt % PCTG 25976, and 0.15 wt % Weston 619 was produced using a1.25 inch single screw extruder. Sheets consisting of the blend werethen produced using a 3.5 inch single screw extruder. A sheet wasextruded continuously, gauged to a thickness of 118 mil and then varioussheets were sheared to size. The glass transition temperature wasmeasured on one sheet and was 117° C. Sheets were then conditioned at50% relative humidity and 60° C. for 4 weeks. The moisture level wasmeasured to be 0.215 wt %. Sheets were subsequently thermoformed into afemale mold having a draw ratio of 2.5:1 using a Brown thermoformingmachine. The thermoforming oven heaters were set to 70/60/60% outputusing top heat only. Sheets were left in the oven for various amounts oftime in order to determine the effect of sheet temperature on the partquality as shown in the table below. Part quality was determined bymeasuring the volume of the thermoformed part, calculating the draw, andvisually inspecting the thermoformed part. The draw was calculated asthe part volume divided by the maximum part volume achieved in this setof experiments (Example A). The thermoformed part was visually inspectedfor any blisters and the degree of blistering rated as none (N), low(L), or high (H). The results below demonstrate that these thermoplasticsheets with a glass transition temperature of 117° C. cannot bethermoformed under the conditions shown below, as evidenced by theinability to produce sheets having greater than 95% draw and noblistering, without predrying the sheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 114 196 813100 H B 100 182 804 99 H C 99 177 801 98 L D 92 171 784 96 L E 82 168727 89 L F 87 166 597 73 N

Example 22 Comparative Example

A miscible blend consisting of 65 wt % Teijin L-1250 polycarbonate,34.85 wt % PCTG 25976, and 0.15 wt % Weston 619 was produced using a1.25 inch single screw extruder. Sheets consisting of the blend werethen produced using a 3.5 inch single screw extruder. A sheet wasextruded continuously, gauged to a thickness of 118 mil and then varioussheets were sheared to size. The glass transition temperature wasmeasured on one sheet and was 120° C. Sheets were then conditioned at50% relative humidity and 60° C. for 4 weeks. The moisture level wasmeasured to be 0.23 wt %. Sheets were subsequently thermoformed into afemale mold having a draw ratio of 2.5:1 using a Brown thermoformingmachine. The thermoforming oven heaters were set to 70/60/60% outputusing top heat only. Sheets were left in the oven for various amounts oftime in order to determine the effect of sheet temperature on the partquality as shown in the table below. Part quality was determined bymeasuring the volume of the thermoformed part, calculating the draw, andvisually inspecting the thermoformed part. The draw was calculated asthe part volume divided by the maximum part volume achieved in this setof experiments (Example A). The thermoformed part was visually inspectedfor any blisters and the degree of blistering rated as none (N), low(L), or high (H). The results below demonstrate that these thermoplasticsheets with a glass transition temperature of 120° C. cannot bethermoformed under the conditions shown below, as evidenced by theinability to produce sheets having greater than 95% draw and noblistering, without predrying the sheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 120 197 825100 H B 101 177 820 99 H C 95 174 781 95 L D 85 171 727 88 L E 83 166558 68 L

Example 23 Comparative Example

A miscible blend consisting of 70 wt % Teijin L-1250 polycarbonate,29.85 wt % PCTG 25976, and 0.15 wt % Weston 619 was produced using a1.25 inch single screw extruder. Sheets consisting of the blend werethen produced using a 3.5 inch single screw extruder. A sheet wasextruded continuously, gauged to a thickness of 118 mil and then varioussheets were sheared to size. The glass transition temperature wasmeasured on one sheet and was 123° C. Sheets were then conditioned at50% relative humidity and 60° C. for 4 weeks. The moisture level wasmeasured to be 0.205 wt %. Sheets were subsequently thermoformed into afemale mold having a draw ratio of 2.5:1 using a Brown thermoformingmachine. The thermoforming oven heaters were set to 70/60/60% outputusing top heat only. Sheets were left in the oven for various amounts oftime in order to determine the effect of sheet temperature on the partquality as shown in the table below. Part quality was determined bymeasuring the volume of the thermoformed part, calculating the draw, andvisually inspecting the thermoformed part. The draw was calculated asthe part volume divided by the maximum part volume achieved in this setof experiments (Examples A and B). The thermoformed part was visuallyinspected for any blisters and the degree of blistering rated as none(N), low (L), or high (H). The results below demonstrate that thesethermoplastic sheets with a glass transition temperature of 123° C.cannot be thermoformed under the conditions shown below, as evidenced bythe inability to produce sheets having greater than 95% draw and noblistering, without predrying the sheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 126 198 826100 H B 111 188 822 100 H C 97 177 787 95 L D 74 166 161 19 L E 58 154 00 NA F 48 149 0 0 NA NA = not applicable. A value of zero indicates thatthe sheet was not formed because it did not pull into the mold (likelybecause it was too cold).

Example 24 Comparative Example

Sheets consisting of Teijin L-1250 polycarbonate were produced using a3.5 inch single screw extruder. A sheet was extruded continuously,gauged to a thickness of 118 mil and then various sheets were sheared tosize. The glass transition temperature was measured on one sheet and was149° C. Sheets were then conditioned at 50% relative humidity and 60° C.for 4 weeks. The moisture level was measured to be 0.16 wt %. Sheetswere subsequently thermoformed into a female mold having a draw ratio of2.5:1 using a Brown thermoforming machine. The thermoforming ovenheaters were set to 70/60/60% output using top heat only. Sheets wereleft in the oven for various amounts of time in order to determine theeffect of sheet temperature on the part quality as shown in the tablebelow. Part quality was determined by measuring the volume of thethermoformed part, calculating the draw and visually inspecting thethermoformed part. The draw was calculated as the part volume divided bythe maximum part volume achieved in this set of experiments (Example A).The thermoformed part was visually inspected for any blisters and thedegree of blistering rated as none (N), low (L), or high (H). Theresults below demonstrate that these thermoplastic sheets with a glasstransition temperature of 149° C. cannot be thermoformed under theconditions shown below, as evidenced by the inability to produce sheetshaving greater than 95% draw and no blistering, without predrying thesheets prior to thermoforming.

Thermoforming Conditions Part Quality Sheet Part Heat Time TemperatureVolume Blisters Example (s) (° C.) (mL) Draw (%) (N, L, H) A 152 216 820100 H B 123 193 805 98 H C 113 191 179 22 H D 106 188 0 0 H E 95 182 0 0NA F 90 171 0 0 NA NA = not applicable. A value of zero indicates thatthe sheet was not formed because it did not pull into the mold (likelybecause it was too cold).

It can be clearly seen from a comparison of the data in the aboverelevant working examples that the polyesters of the present inventionoffer a definite advantage over the commercially available polyesterswith regard to glass transition temperature, density, slowcrystallization rate, melt viscosity, and toughness.

The invention has been described in detail with reference to theembodiments disclosed herein, but it will be understood that variationsand modifications can be effected within the spirit and scope of theinvention.

1. A polyester composition comprising at least one polyester whichcomprises: (a) a dicarboxylic acid component comprising: i) 80 to 100mole % of terephthalic acid residues; ii) 0 to 20 mole % of aromaticdicarboxylic acid residues having up to 20 carbon atoms; and iii) 0 to10 mole % of aliphatic dicarboxylic acid residues having up to 16 carbonatoms; and (b) a glycol component comprising: i) 20 to 30 mole % of2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and ii) 70 to 80 mole% of 1,4-cyclohexanedimethanol residues, wherein the total mole % of thedicarboxylic acid component is 100 mole %, and the total mole % of theglycol component is 100 mole %; wherein the inherent viscosity of saidpolyester is from 0.60 to 0.75 dL/g as determined in 60/40 (wt/wt)phenol/tetrachloroethane at a concentration of 0.5 g/100 ml at 25° C.;wherein said polyester has a Tg of 100 to 130° C.; wherein saidpolyester has a notched Izod impact strength of at least 7.5 ft-lb/inchat 23° C. according to ASTM D256 with a 10-mil notch in a ⅛-inch thickbar; wherein the melt viscosity of said polyester is less than 10,000poise as measured at 1 radian/second on a rotary melt rheometer at 290°C.; and wherein said polyester composition contains no polycarbonate. 2.The polyester composition of claim 1, wherein the inherent viscosity isfrom 0.65 to 0.75 dL/g.
 3. The polyester composition of claim 1, whereinthe glycol component comprises 25 to 30 mole %2,2,4,4-tetramethyl-1,3-cyclobutanediol residues and 70 to 75 mole %1,4-cyclohexanedimethanol residues.
 4. The polyester composition ofclaim 1, wherein the glycol component of said polyester comprises 20 to25 mole % 2,2,4,4-tetramethyl-1,3-cyclobutanediol residues and 75 to 80mole % 1,4-cyclohexanedimethanol residues.
 5. The polyester compositionof claim 1, wherein said polyester has a Tg of 100 to 120° C.
 6. Thepolyester composition of claim 1, wherein said polyester has a Tg of 105to 120° C.
 7. The polyester composition of claim 1, wherein thedicarboxylic acid component comprises 90 to 100 mole % of terephthalicacid residues.
 8. The polyester composition of claim 1, wherein saidpolyester comprises 1,3-propanediol residues, 1,4-butanediol residues,or mixture thereof
 9. The polyester composition of claim 1, wherein saidpolyester comprises from 0.01 to 15 mole % of ethylene glycol residues.10. The polyester composition of claim 1, wherein said2,2,4,4tetramethyl-1,3-cyclobutanediol is a mixture comprising greaterthan 50 mole % of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol and lessthan 50 mole % of trans-2,2,4,4tetramethyl-1,3-cyclobutanediol.
 11. Thepolyester composition of claim 1, wherein said2,2,4,4tetramethyl-1,3-cyclobutanediol is a mixture comprising from 30to 70 mole % of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol and from 70to 30 mole % of trans-2,2,4,4tetramethyl-1,3-cyclobutanediol.
 12. Thepolyester composition of claim 11, wherein said2,2,4,4-tetramethyl-1,3-cyclobutanediol is a mixture comprising from 40to 60 mole % of cis-2,2,4,4-tetramethyl-1,3-cyclobutanediol and from 60to 40 mole % of trans-2,2,4,4tetramethyl-1,3-cyclobutanediol.
 13. Thepolyester composition of claim 1, wherein said polyester compositioncomprises at least one polymer chosen from at least one of thefollowing: poly(etherimides), polyphenylene oxides, poly(phenyleneoxide)/polystyrene blends, polystyrene resins, polyphenylene sulfides,polyphenylene sulfide/sulfones, polysulfones; polysulfone ethers, andpoly(ether-ketones).
 14. The polyester composition of claim 1, whereinsaid polyester comprises residues of at least one branching agent. 15.The polyester composition of claim 14, wherein said polyester comprisesresidues of at least one branching agent an amount of 0.01 to 10 mole %based on the total mole percentage of the diacid or diol residues. 16.The polyester composition of claim 1, wherein said polyester has acrystallization half-time of greater than 5 minutes at 170° C.
 17. Thepolyester composition of claim 1, wherein said polyester composition hasa density of less than 1.2 g/ml at 23° C.
 18. The polyester compositionof claim 1, wherein said polyester composition comprises at least onethermal stabilizer or reaction products thereof.
 19. The polyestercomposition of claim 1, having a b* value of from −10 to less than 10and the L* values can be from 50 to 90 according to the L*, a* and b*color system of the CIE (International Commission on Illumination). 20.The polyester composition of claim 1, wherein said polyester has anotched Izod impact strength of at least 10 ft-lbs/in at 23° C.according to ASTM D256 with a 10-mil notch in a ⅛-inch thick bar. 21.The polyester composition of claim 1, wherein the polyester comprisesthe residue of at least one catalyst comprising a tin compound or areaction product thereof.
 22. An article of manufacture comprising thepolyester composition of claim
 1. 23. A polyester composition comprisingat least one polyester which comprises: (a) a dicarboxylic acidcomponent comprising: i) 80 to 100 mole % of terephthalic acid residues;ii) 0 to 20 mole % of aromatic dicarboxylic acid residues having up to20 carbon atoms; and iii) 0 to 10 mole % of aliphatic dicarboxylic acidresidues having up to 16 carbon atoms; and (b) a glycol componentcomprising: i) 20 to 30 mole % of2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and ii) 70 to 80 mole% of 1,4-cyclohexanedimethanol residues, wherein the total mole % of thedicarboxylic acid component is 100 mole %, and the total mole % of theglycol component is 100 mole %; wherein the inherent viscosity of saidpolyester is from 0.65 to 0.75 dL/g as determined in 60/40 (wt/wt)phenol/tetrachloroethane at a concentration of 0.5 g/100 ml at 25° C.;wherein said polyester has a Tg of 100 to 130° C.; wherein saidpolyester has a notched Izod impact strength of at least 7.5 ft-lb/inchat 23° C. according to ASTM D256 with a 10-mil notch in a ⅛-inch thickbar at 23° C.; wherein the melt viscosity of said polyester is less than10,000 poise as measured at 1 radian/second on a rotary melt rheometerat 290° C.; and wherein said polyester composition contains nopolycarbonate.
 24. The polyester composition of claim 23, wherein saidpolyester has a Tg of 100 to 120° C.
 25. The polyester composition ofclaim 23, wherein said polyester has a Tg of 100 to 115° C.
 26. Apolyester composition comprising at least one polyester which comprises:(a) a dicarboxylic acid component comprising: i) 80 to 100 mole % ofterephthalic acid residues; ii) 0 to 20 mole % of aromatic dicarboxylicacid residues having up to 20 carbon atoms; and iii) 0 to 10 mole % ofaliphatic dicarboxylic acid residues having up to 16 carbon atoms; and(b) a glycol component comprising: i) 20 to 30 mole % of2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and ii) 70 to 80 mole% of 1,4-cyclohexanedimethanol residues, iii) 0.01 to less than 15 mole% ethylene glycol residues; wherein the total mole % of the dicarboxylicacid component is 100 mole %, and the total mole % of the glycolcomponent is 100 mole %; wherein the inherent viscosity of saidpolyester is from 0.60 to 0.75 dL/g as determined in 60/40 (wt/wt)phenol/tetrachloroethane at a concentration of 0.5 g/100 ml at 25° C.;wherein said polyester has a Tg of 100 to 130° C.; wherein saidpolyester has a notched Izod impact strength of at least 7.5 ft-lb/inchat 23° C. according to ASTM D256 with a 10-mil notch in a ⅛-inch thickbar; wherein the melt viscosity of said polyester is less than 10,000poise as measured at 1 radian/second on a rotary melt rheometer at 290°C.; and wherein said polyester composition contains no polycarbonate.27. A polyester composition comprising at least one polyester whichcomprises: (a) a dicarboxylic acid component comprising: i) 80 to 100mole % of terephthalic acid residues; ii) 0 to 20 mole % of aromaticdicarboxylic acid residues having up to 20 carbon atoms; and iii) 0 to10 mole % of aliphatic dicarboxylic acid residues having up to 16 carbonatoms; (b) a glycol component comprising: i) 20 to 30 mole % of2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and ii) 70 to 80 mole% of 1,4-cyclohexanedimethanol residues, and (c) residues of at leastone branching agent in the amount of 0.01 to 10 mole % based on thetotal mole percentage of the diacid residues or diol residues; whereinthe total mole % of the dicarboxylic acid component is 100 mole %, andthe total mole % of the glycol component is 100 mole %; wherein theinherent viscosity of said polyester is from 0.60 to 0.75 dL/g asdetermined in 60/40 (wt/wt) phenol/tetrachloroethane at a concentrationof 0.5 g/100 ml at 25° C.; wherein said polyester has a Tg of 100 to130° C.; wherein said polyester has a notched Izod impact strength of atleast 7.5 ft-lb/inch at 23° C. according to ASTM D256 with a 10-milnotch in a ⅛-inch thick bar; wherein the melt viscosity of saidpolyester is less than 10,000 poise as measured at 1 radian/second on arotary melt rheometer at 290° C.; and wherein said polyester compositioncontains no polycarbonate.
 28. A polyester composition comprising: (I)at least one polyester which comprises: (a) a dicarboxylic acidcomponent comprising: i) 80 to 100 mole % of terephthalic acid residues;ii) 0 to 20 mole % of aromatic dicarboxylic acid residues having up to20 carbon atoms; and iii) 0 to 10 mole % of aliphatic dicarboxylic acidresidues having up to 16 carbon atoms; and (b) a glycol componentcomprising: i) 20 to 30 mole % of2,2,4,4-tetramethyl-1,3-cyclobutanediol residues; and ii) 70 to 80 mole% of 1,4-cyclohexanedimethanol residues; and (II) at least one thermalstabilizer or the reaction product thereof chosen from at least one ofphosphoric acid, phosphorous acid, phosphoric acid, phosphinic acid,phosphonous acid, or an ester or salt thereof; wherein the total mole %of the dicarboxylic acid component is 100 mole %, and the total mole %of the glycol component is 100 mole %; wherein the inherent viscosity ofsaid polyester is from 0.60 to 0.75 dL/g as determined in 60/40 (wt/wt)phenol/tetrachloroethane at a concentration of 0.5 g/100 ml at 25° C.;wherein said polyester has a Tg of 100 to 130° C.; wherein saidpolyester has a notched Izod impact strength of at least 7.5 ft-lb/inchat 23° C. according to ASTM D256 with a 10-mil notch in a ⅛-inch thickbar; wherein the melt viscosity of said polyester is less than 10,000poise as measured at 1 radian/second on a rotary melt rheometer at 290°C.; and wherein said polyester composition contains no polycarbonate.29. The polyester composition of claim 28, wherein the polyestercomposition comprises residues from at least one branching agent in theamount of 0.01 to 10 mole % based on the total mole percentage of thediacid residues or diol residues.
 30. The polyester composition of claim28, wherein the polyester composition comprises at least one additivechosen from colorants, dyes, mold release agents, flame retardants,plasticizers, nucleating agents, UV stabilizers, glass fiber, carbonfilaments, fillers, impact modifiers, and mixtures thereof.
 31. Thepolyester composition of claim 28, wherein the polyester comprises from0.01 to 15 mole % of ethylene glycol residues.
 32. The polyestercomposition of claim 1, wherein the polyester composition comprises atleast one additive chosen from colorants, dyes, mold release agents,flame retardants, plasticizers, nucleating agents, UV stabilizers, glassfiber, carbon filaments, fillers, impact modifiers, and mixturesthereof.
 33. The polyester composition of claim 1, wherein saidpolyester has a notched Izod impact strength of at least 18 ft-lbs/in at23° C. according to ASTM D256 with a 10-mil notch in a ⅛-inch thick bar.34. The polyester composition of claim 1, wherein the melt viscosity ofsaid polyester is less than 6,000 poise as measured at 1 radian/secondon a rotary melt rheometer at 290° C.
 35. The polyester composition ofclaim 23, wherein said polyester has a notched Izod impact strength ofat least 10 ft-lbs/in at 23° C. according to ASTM D256 with a 10-milnotch in a ⅛-inch thick bar.
 36. The polyester composition of claim 23,wherein the melt viscosity of said polyester is less than 6,000 poise asmeasured at 1 radian/second on a rotary melt rheometer at 290° C.